CN112139242A - Steel for large heat input welding and method for improving toughness of heat affected zone of steel - Google Patents
Steel for large heat input welding and method for improving toughness of heat affected zone of steel Download PDFInfo
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- CN112139242A CN112139242A CN202010858392.0A CN202010858392A CN112139242A CN 112139242 A CN112139242 A CN 112139242A CN 202010858392 A CN202010858392 A CN 202010858392A CN 112139242 A CN112139242 A CN 112139242A
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- 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
- B21B1/22—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 plates, strips, bands or sheets of indefinite length
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- 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
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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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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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
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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
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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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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- 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
- B21B1/22—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 plates, strips, bands or sheets of indefinite length
- B21B2001/225—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 plates, strips, bands or sheets of indefinite length by hot-rolling
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- 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
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- 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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Abstract
The invention discloses steel for large heat input welding and a method for improving the toughness of a heat affected zone thereof, which are characterized in that after the reasonable process links of component design, casting, rolling and cooling are controlled, fine and dispersed (Ti, Si, Al and Mn) O, MnS type inclusions are formed in a base metal, the size of the inclusions is more between 0.5 and 2 mu m, and a large amount of long and thin Acicular Ferrite (AF) tissues are generated by taking the inclusions as cores, so that the base metal has higher mechanical property. After high heat input welding of 200-800 kJ/cm, AF structures in a welding affected zone (HAZ) are converted into equiaxed ferrite structures, the-40 ℃ low-temperature impact toughness of the HAZ is not reduced, but is slightly increased, the HAZ toughness is not affected by welding heat input, the welding efficiency is greatly improved, and meanwhile the HAZ has stable mechanical properties.
Description
Technical Field
The invention belongs to the technical field of low-alloy high-strength steel welding, and particularly relates to steel for large heat input welding and a heat affected zone toughness improving method thereof, which can improve welding efficiency and improve heat affected zone toughness.
Background
In the field of manufacturing large equipment machines such as shipbuilding, offshore platforms, and oil storage tanks, welding is increasingly regarded as an important link of production and processing, and with the increase in size and strength of processing members, welding construction efficiency is improved and production and manufacturing costs are reduced. Under the background, large heat input welding methods such as electro-gas welding, electroslag welding and submerged arc welding are widely applied in the manufacturing field related to medium and heavy plates, but when the welding heat input is increased, the peak temperature of the welding heat cycle experienced by a welding joint is increased, so that the cooling speed is reduced, the grain structure of a welding Heat Affected Zone (HAZ) is easily coarse, the HAZ structure is uneven, the mechanical property is further influenced, and the method becomes a key problem for limiting the further popularization and application of the large heat input welding technology.
In order to solve the problem of low mechanical property of large heat input welding HAZ, related scholars at home and abroad put forward an oxide metallurgy concept, and by adding a large amount of non-metallic inclusions into steel, AF structure nucleation can be induced to grow, so that the aims of refining HAZ crystal grain structure and improving HAZ low-temperature impact toughness are fulfilled. TiN, as the earliest inclusion in the oxide metallurgy technology, has obvious effect under the condition of peak temperature below 1300 ℃, but when the welding heat input is increased, the temperature of a welding fusion line easily exceeds 1400 ℃, the temperature exceeds the melting point of TiN, most of TiN is dissolved and dissolved, and the effect of inducing AF structure nucleation is lost. Later, Ti oxides are gradually adopted to replace TiN as inclusions, although the melting point of Ti oxides exceeds 1400 ℃, when the welding peak temperature exceeds 1400 ℃, the inclusions can exist stably, but the Ti oxides are difficult to disperse in steel finely and easily aggregate to form large-size inclusions, and when HAZ bears external stress, the inclusions of the type can easily become crack sources to influence the mechanical property of HAZ. Therefore, the development of steel for high heat input welding having excellent HAZ performance has been the direction of the researchers.
Disclosure of Invention
The invention provides steel for large heat input welding and a heat affected zone toughness improving method thereof, aiming at solving the problem that the toughness of the heat affected zone of the steel for large heat input welding is low.
The method is different from the previous research, an AF structure can be directly formed in a rolled welding base metal through reasonable components and preparation process design, after high heat input welding of 200-800 kJ/cm, the HAZ microstructure is converted into an equiaxed ferrite structure, the-40 ℃ low-temperature impact energy is not reduced, but is slightly increased, and after the welding heat input is increased, the HAZ microstructure is not coarsened, and the-40 ℃ low-temperature impact energy is kept stable.
The steel for high heat input welding takes improvement of HAZ low-temperature impact toughness as a research and development target, optimizes the design of alloy components on the basis of comprehensively considering the influence of various alloy elements on the HAZ impact toughness of high heat input welding, and comprises the following chemical components in percentage by mass: c: 0.06% -0.12%, Si: 0.10-0.40%, Mn: 0.80% -2.30%, Al: 0.03% -0.06%, P: less than or equal to 0.015 percent, S: less than or equal to 0.013 percent, Ti: 0.05% -0.15%, B: 0.002% -0.005% and the balance of Fe, wherein the balance of Fe is doped with a very small amount of inevitable impurities.
The design of the steel for high heat input welding of the invention comprises the following components:
c: the steel plate is a strong solid solution strengthening element and has strong hardenability, the strength of the steel plate can not be ensured when the content is too low, and if the content of C is too high, a large amount of M-A island structures are formed, the welding crack sensitivity is increased, and the HAZ impact toughness is influenced.
Si: is an important deoxidizing element in steel, is also a constituent element of inclusions, and can promote the generation of AF structures. If the Si content is too low, the deoxidation effect cannot be effectively exerted, and if the Si content is too high, solid solution strengthening and the second phase content increase, and a hard M-a structure is easily formed, increasing the strength and hardness, and deteriorating the toughness.
Mn: for the steel for high heat input welding, measures of reducing C and increasing Mn can be adopted to improve the low-temperature impact toughness, and the proper amount of Mn is added to increase the content of AF and be beneficial to improving the impact toughness while ensuring the strength.
Al: on the other hand, Al has the highest affinity with O, and is usually added as a deoxidizer to form Al2O3, which is an important component of inclusions. On the other hand, Al fixes N atoms in interstitial atoms and promotes the formation of Ti compounds.
P: the content of the element is controlled to 0.015% or less, which inevitably causes the steel sheet to have increased strength and reduced low-temperature impact toughness.
S: s and P are inevitable impurity elements, and if S is contained in a proper amount, sulfides such as CuS, CaS and the like with high melting points are formed to become the AF nucleation core. The most common S element is attached around the oxide inclusion in the form of MnS, and promotes the nucleation and growth of AF in weld metal. If the S content is too high, coarse MnS and CaS inclusions are generated, and the inclusions themselves have high hardness and are preferentially separated from the matrix during fracture to become starting points of cracks, thereby significantly increasing the weld crack sensitivity.
Ti: the Ti is the most commonly used microalloy element in the steel for high heat input welding, and a proper amount of Ti is beneficial to promoting the formation of inclusions and the phase transformation of AF structure, so that the excessive Ti is easy to be dissolved in a matrix, and the HAZ toughness is reduced.
B: the size of atoms is small, solid-dissolved B is easy to diffuse to austenite grain boundaries, the phase transition temperature of ferrite is reduced while the interface energy is reduced, and therefore the generation of grain boundary ferrite is inhibited, and AF structure phase transition is promoted. And B and N are combined into BN, so that the harm of solid solution N is reduced, and the toughness is improved in multiple angles.
A method for improving the toughness of a heat affected zone of steel for large heat input welding is characterized by comprising the following steps: which comprises the following steps:
(1) smelting: according to the component design of the steel for high heat input welding, various raw materials are subjected to alloy smelting at 1600-1700 ℃, molten steel is smelted, and steel ingots are obtained by casting;
(2) rolling: heating the steel ingot to 1200 ℃, preserving heat for 2-4 h, performing two-stage controlled rolling of rough rolling and finish rolling after full austenitizing to form a rolled plate;
(3) and (3) cooling: and cooling the rolled plate by adopting a laminar cooling mode.
As a possible implementation manner, further, in the step (2), the rough rolling initial rolling temperature is 1150-1050 ℃, the pass deformation is 20-50%, and a rough rolled plate is obtained; and (3) carrying out multi-pass finish rolling at the initial rolling temperature of 880-900 ℃ and the pass deformation of 50-80% to obtain the required rolled plate.
As a possible implementation manner, further, in the step (3), the cooling starting temperature after rolling is 800-820 ℃, the cooling speed is 1-10 ℃/s, the final cooling temperature is 480-520 ℃, and finally, the steel is air-cooled to the room temperature to obtain the steel for large heat input welding.
By adopting the technical scheme, compared with the prior art, the invention has the beneficial effects that:
according to the scheme, after the reasonable component design, pouring, rolling and cooling process links are controlled, fine and dispersed (Ti, Si, Al and Mn) O, MnS-type inclusions are formed in the base metal, the size of the inclusions is more than 0.5-2 mu m, and a large amount of long and thin Acicular Ferrite (AF) structures are generated by taking the inclusions as cores, so that the base metal has high mechanical properties. After high heat input welding of 200-800 kJ/cm, AF structures in a welding affected zone (HAZ) are converted into equiaxed ferrite structures, the-40 ℃ low-temperature impact toughness of the HAZ is not reduced, but is slightly increased, the HAZ toughness is not affected by welding heat input, the welding efficiency is greatly improved, and meanwhile the HAZ has stable mechanical properties.
The traditional steel for high heat input welding is developed by adopting an oxide metallurgy technology, a rolling state base material mainly comprising a ferrite pearlite structure is formed by adding a part of inclusions in the steel, and the inclusions in the HAZ can induce the phase transformation of a slender AF structure in the heat cycle cooling process of the high heat input welding so as to toughen the HAZ, but the toughness of the HAZ is reduced relative to the base material, and particularly under the high heat input welding condition of more than 500kJ/cm, the toughness of the HAZ is difficult to meet the standard use requirement. Compared with the traditional steel for large heat input welding, the steel for large heat input welding is prepared by using the technology of oxide metallurgy, and the differences are as follows: after the component design and preparation process provided by the invention is adopted, the type of the inclusion in the steel is the inclusion in the composite form of (Ti, Si, Al and Mn) O, MnS, the distribution quantity is greatly increased, the structure of the base metal directly forms a slender AF structure, after high heat input welding, the AF structure is converted into an equiaxial ferrite structure, the impact toughness is not reduced and is not increased, and the effect cannot be realized by other steel types.
The scheme is particularly suitable for welding the large equipment such as shipbuilding, ocean platforms and buildings with the thickness of 20-100 mm, the heat input is in the range of 200-800 kJ/cm, the welding manufacturing efficiency is greatly improved, and meanwhile, the low-temperature impact toughness of HAZ can be effectively guaranteed.
Drawings
The invention will be further explained with reference to the drawings and the detailed description below:
FIG. 1 is a schematic view showing the microstructure of a large heat input welding steel as a base material according to an embodiment of the present invention;
FIG. 2 is a schematic view showing the HAZ microstructure of the steel for high heat input welding according to the embodiment of the present invention after the welding heat cycle of 800 kJ/cm.
Detailed Description
A method for improving the toughness of a heat affected zone of steel for large heat input welding comprises the following chemical compositions: c: 0.08%, Si: 0.23%, Mn: 1.80%, Al: 0.035%, P: less than or equal to 0.015 percent, S: less than or equal to 0.013 percent, Ti: 0.07%, B: 0.002, and the balance being Fe, wherein the balance Fe contains a trace of unavoidable impurities.
The method for improving the toughness of the heat affected zone of the steel for the large heat input welding comprises the following specific steps:
(1) smelting: according to the component design of the steel for high heat input welding, various raw materials are subjected to alloy smelting at 1600 ℃, molten steel is smelted, and a steel ingot is obtained by casting;
(2) rolling: heating the steel ingot to 1200 ℃, preserving heat for 2 hours, and after full austenitizing, carrying out 2-pass rough rolling on the steel ingot, wherein the initial rolling temperature of the rough rolling is 1100 ℃, the final rolling temperature is 1050 ℃, the single-pass reduction rate is 25%, and the total cumulative reduction rate is 50% to obtain a rough rolling plate; and (3) carrying out 3-pass finish rolling on the cold-rolled plate, wherein the start rolling temperature of the finish rolling is 900 ℃, the finish rolling temperature is 880 ℃, the single-pass reduction rate is 20%, and the total cumulative reduction rate is 60% to obtain the finish-rolled plate.
(3) And (3) cooling: and cooling the rolled plate by adopting a laminar cooling mode, wherein the cooling starting temperature is 800 ℃, the cooling speed is 5 ℃/s, and the final cooling temperature is 510 ℃, so that the steel for large heat input welding with the thickness of 20 mm is obtained.
The mechanical properties of the rolled parent metal in the embodiment are respectively as follows: rel (458MPa), Rm (585MPa), (24%), Akv (-40 ℃, 169J), fig. 1 is a parent material microstructure, all elongated AF tissues; after high heat input welding of 500kJ/cm, the impact energy of HAZ at-40 ℃ is 172J, after high heat input welding of 800kJ/cm, the impact energy of HAZ at-40 ℃ is 179J, and FIG. 2 shows that after welding heat circulation of 800kJ/cm, the HAZ microstructure is completely converted into an equiaxed ferrite structure, and the equiaxed ferrite structure can effectively improve the HAZ impact toughness.
The foregoing is directed to embodiments of the present invention, and equivalents, modifications, substitutions and variations such as will occur to those skilled in the art, which fall within the scope and spirit of the appended claims.
Claims (7)
1. A steel for high heat input welding, characterized in that: it includes: the chemical composition mass fraction is as follows:
C：0.06％～0 .12％；
Si：0.10％～0.40％；
Mn：0.80％～2.30％；
Al：0.03％～0.06％；
P：≤0.015％；
S：≤0.013％；
Ti：0.05％～0.15％；
B：0.002％～0.005％；
the balance being Fe.
2. The steel for high heat input welding according to claim 1, characterized in that: the balance of Fe is also doped with fine dispersed (Ti, Si, Al, Mn) O, MnS type inclusions with the size of 0.5-2 μm.
3. The steel for high heat input welding according to claim 1, characterized in that: the tensile strength of a base material formed by the steel for high heat input welding is 500-650 MPa, and after the steel is subjected to high heat input welding of 200-800 kJ/cm, the HAZ-40 ℃ impact energy is greater than 120J.
4. The method for improving the toughness of the heat-affected zone of the steel for the large heat input welding according to claim 1, wherein the method comprises the following steps: the microstructure of a rolled steel plate formed by the steel for high heat input welding is a slender AF structure, and after the steel is subjected to high heat input welding of 200-800 kJ/cm, the HAZ of the steel is an equiaxed ferrite structure and is not coarsened along with the increase of heat input.
5. The method for improving the toughness of the heat affected zone of the steel for the high heat input welding according to one of claims 1 to 4, characterized by comprising the following steps: which comprises the following steps:
(1) smelting: according to the component design of the steel for high heat input welding, various raw materials are subjected to alloy smelting at 1600-1700 ℃, molten steel is smelted, and steel ingots are obtained by casting;
(2) rolling: heating the steel ingot to 1200 ℃, preserving heat for 2-4 h, performing two-stage controlled rolling of rough rolling and finish rolling after full austenitizing to form a rolled plate;
(3) and (3) cooling: and cooling the rolled plate by adopting a laminar cooling mode.
6. The method for improving the toughness of the heat-affected zone of the steel for the large heat input welding according to claim 5, wherein the method comprises the following steps: in the step (2), the initial rolling temperature of rough rolling is 1150-1050 ℃, the pass deformation is 20-50%, and a rough rolling plate is obtained; and (3) carrying out multi-pass finish rolling at the initial rolling temperature of 880-900 ℃ and the pass deformation of 50-80% to obtain the required rolled plate.
7. The method for improving the toughness of the heat-affected zone of the steel for the large heat input welding according to claim 5, wherein the method comprises the following steps: and (3) after rolling, cooling at the starting temperature of 800-820 ℃, the cooling speed of 1-10 ℃/s, the final cooling temperature of 480-520 ℃, and finally air cooling to room temperature to obtain the high heat input welding steel.
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| CN102766748A (en) * | 2012-08-10 | 2012-11-07 | 江苏省沙钢钢铁研究院有限公司 | Production method of low-temperature steel plate capable of being welded at high heat input |
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| CN106702265A (en) * | 2016-12-13 | 2017-05-24 | 苏州纽东精密制造科技有限公司 | High-strength ship plate steel |
| CN108359903A (en) * | 2018-04-13 | 2018-08-03 | 沈阳工业大学 | A kind of low-alloy high-strength steel and its high heat-input welding heat affected zone toughening method |
| CN109321815A (en) * | 2017-07-31 | 2019-02-12 | 东北大学 | A kind of manufacturing method of resistance to Large Heat Input Welding high-strength steel plate |
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2020
- 2020-08-24 CN CN202010858392.0A patent/CN112139242B/en active Active
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH08283904A (en) * | 1995-04-17 | 1996-10-29 | Nippon Steel Corp | Steel material excellent in toughness in weld heat-affected zone and its production |
| JPH11236645A (en) * | 1998-02-24 | 1999-08-31 | Nippon Steel Corp | High tensile strength steel for welding excellent in toughness in extra-large heat input weld heat-affected zone |
| CN102080189A (en) * | 2011-01-10 | 2011-06-01 | 东北大学 | Structural steel for high-heat input welding and manufacturing method thereof |
| JP2013147740A (en) * | 2011-12-19 | 2013-08-01 | Jfe Steel Corp | Steel material for heavy heat input welding |
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| CN102766748A (en) * | 2012-08-10 | 2012-11-07 | 江苏省沙钢钢铁研究院有限公司 | Production method of low-temperature steel plate capable of being welded at high heat input |
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| CN109321815A (en) * | 2017-07-31 | 2019-02-12 | 东北大学 | A kind of manufacturing method of resistance to Large Heat Input Welding high-strength steel plate |
| CN108359903A (en) * | 2018-04-13 | 2018-08-03 | 沈阳工业大学 | A kind of low-alloy high-strength steel and its high heat-input welding heat affected zone toughening method |
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