CN111910127B - Q890 steel plate for hydraulic support meeting welding heat input of 30kJ/cm and preparation method thereof - Google Patents
Q890 steel plate for hydraulic support meeting welding heat input of 30kJ/cm and preparation method thereof Download PDFInfo
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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
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- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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Abstract
The invention relates to a Q890 steel plate for a hydraulic support meeting the welding heat input of 30kJ/cm and a preparation method thereof, belonging to the technical field of ferrous metallurgy and high-strength steel welding. The steel plate comprises the following chemical components in percentage by weight: 0.12 to 0.13% of C, 0.30 to 0.35% of Si, 1.5 to 1.6% of Mn, less than or equal to 0.012% of P, less than or equal to 0.008% of S, 0.5 to 0.6% of Mo, 0.08 to 0.09% of V, 0.0005 to 0.0012% of B, 0.02 to 0.03% of Zr, 0.02 to 0.03% of Ti, and the balance of Fe and inevitable impurities. The yield strength of the steel plate prepared by the invention reaches 900MPa, the tensile strength reaches 1000MPa, the elongation after fracture is 16%, the impact energy at minus 20 ℃ is 200J, and the welding heat input reaches 30 kJ/cm.
Description
Technical Field
The invention belongs to the technical field of ferrous metallurgy and high-strength steel welding, and particularly relates to a Q890 steel plate for a hydraulic support with welding heat input of 30kJ/cm and a preparation method thereof.
Background
Along with the deepening of coal mining and the increase of excavation amount, the hydraulic support is developed in the direction of high reliability and large working face, meanwhile, as the key equipment for fully mechanized coal mining, the long service life and light weight of the hydraulic support are also one of important development directions, the main structural components of the existing hydraulic support, such as the top beam, the shield beam, the base, the connecting rod and the like, are also manufactured by adopting high-strength steel plates with the yield strength of 690MPa or below in a large quantity, and through the verification of the strength and the working condition, under the same working condition, if the Q890 steel plate with higher grade is adopted to replace the prior Q690 steel plate, can save 22.5 percent of steel and 37.8 percent of welding material, and ensure that the hydraulic support has higher obdurability, the comprehensive properties of the steel such as the compression resistance, the service life, the use safety and the like can be greatly improved, so that the research, development and popularization of the steel for the hydraulic support with higher grade have important significance.
For the steel for the Q890 hydraulic support, in addition to the requirement of higher strength, the welding performance is an important performance index influencing the large-scale popularization and application, and the reference 1: the effect of weld heat input on crack propagation in the heat affected zone of Q890 high strength steel, reported in weld, 2017,38(8), indicates: with the increase of welding heat input, the microstructure of the coarse crystal area shows the transformation from a martensite structure to a martensite and bainite mixed structure and then to a bainite and granular bainite mixed structure, the welding heat input value can only reach 20kJ/cm, and a large number of M-A components distributed in a chain shape exist in the microstructure under the condition of higher heat input, and belong to brittle fracture. Reference 2: the influence of heat input on the welding performance of the Q890D low-alloy high-strength steel, welding, 2019,3 shows that: when the welding heat input is high, in addition to poor impact toughness, the hardness of the heat affected zone of the backing weld bead is lower than that of the weld joint and the base metal, and the softening phenomenon after welding exists, so that the corresponding welding heat input value is controlled in a lower range. However, when the welding heat input value is low, the cooling speed is high, the hydrogen content of deposited metal is high, and the sensitivity of cold cracks is increased. Therefore, it is necessary to develop a steel plate capable of satisfying high welding heat input, which does not affect the overall performance of the steel plate under the condition of high welding heat input, and can solve the problems existing under the condition of low welding heat input, so that the steel plate can be widely popularized and used.
Chinese patents CN103589969A and CN103555911A respectively disclose a production method of a quenched and tempered high-strength Q890D super-thick steel plate and a production method of a quenched and tempered high-strength Q890E super-thick steel plate, wherein alloy elements such as Cu, Ni, Nb, V, Ti, Cr, Mo and the like are added in the design of alloy components, the specific process is tempering treatment at the temperature of 630-. From the aspect of the thickness specification and the performance index of the final product, the product does not belong to the steel grade for the hydraulic support, and the preparation method of the high-welding heat input steel plate is not involved.
Chinese patent CN106148822A discloses a method for producing a high-strength steel Q890 medium plate by on-line quenching, which focuses on parameters such as slab heating temperature, rolling process and the like, wherein the tempering temperature after quenching is 500 ℃, and the final steel plate structure is a dual-phase structure of lath martensite and lath bainite. Chinese patent CN105880834A discloses a welding method of Q890 high-strength steel, wherein the welding preheating temperature of a steel plate is 60-100 ℃, the interlayer temperature is controlled at 150-250 ℃, and the welded steel plate is tempered. Similarly, neither of the above patents relates to the method for designing the composition and controlling the production process of the Q890 steel sheet having a large welding heat input.
As described above, no clear description is given to the related documents and patents regarding the Q890 steel sheet for hydraulic brackets having a large welding heat input performance.
Disclosure of Invention
The invention aims to provide a Q890 steel plate for a hydraulic bracket meeting the welding heat input of 30kJ/cm on the one hand and a preparation method of the steel plate on the other hand. According to the invention, by designing the components of the steel plate and regulating and controlling the preparation process, the prepared steel plate has good comprehensive use performance on the basis of having the conventional Q890 mechanical property under the condition of ensuring the welding heat input value to be improved, so that the steel plate is popularized and used in a large range.
In order to achieve the purpose, the technical scheme of the invention is as follows:
a Q890 steel plate for a hydraulic bracket meeting the welding heat input of 30kJ/cm comprises the following chemical components in percentage by weight: 0.12 to 0.13% of C, 0.30 to 0.35% of Si, 1.5 to 1.6% of Mn, less than or equal to 0.012% of P, less than or equal to 0.008% of S, 0.5 to 0.6% of Mo, 0.08 to 0.09% of V, 0.0005 to 0.0012% of B, 0.02 to 0.03% of Zr, 0.02 to 0.03% of Ti, and the balance of Fe and inevitable impurities.
Furthermore, the yield strength of the steel plate reaches 900MPa, the tensile strength reaches 1000MPa, the elongation after fracture is 16%, the impact energy at minus 20 ℃ is 200J, and the welding heat input reaches 30kJ/cm, namely the steel plate has good comprehensive performance under the condition that the welding heat input is 30 kJ/cm.
Further, the steel plate may further include: 0.12-0.13% of C, 0.30-0.35% of Si, 1.5-1.6% of Mn, less than or equal to 0.012% of P, less than or equal to 0.008% of S, 0.5-0.6% of Mo, 0.08-0.09% of V, 0.0006-0.0010% of B, 0.02-0.03% of Zr, 0.02-0.03% of Ti, and the balance of Fe and inevitable impurities.
Further, the steel plate may further include: 0.12-0.13% of C, 0.30-0.35% of Si, 1.5-1.6% of Mn, less than or equal to 0.010% of P, less than or equal to 0.005% of S, 0.5-0.6% of Mo, 0.08-0.09% of V, 0.0006-0.0010% of B, 0.02-0.03% of Zr, 0.02-0.03% of Ti, and the balance of Fe and inevitable impurities.
Further, the steel sheet may further have the following composition: 0.12% of C, 0.35% of Si, 1.5% of Mn, 0.008% of P, 0.005% of S, 0.5% of Mo, 0.08% of V, 0.0006% of B, 0.02% of Zr, 0.02% of Ti, and the balance of Fe and inevitable impurities.
Further, the steel sheet may further have the following composition: 0.13% of C, 0.30% of Si, 1.6% of Mn, 0.009% of P, 0.004% of S, 0.6% of Mo, 0.08% of V, 0.0008% of B, 0.03% of Zr, 0.02% of Ti, and the balance of Fe and inevitable impurities.
Further, the steel sheet may further have the following composition: 0.12% of C, 0.33% of Si, 1.5% of Mn, 0.010% of P, 0.004% of S, 0.55% of Mo, 0.09% of V, 0.0010% of B, 0.02% of Zr, 0.03% of Ti, and the balance of Fe and inevitable impurities.
A preparation method of a Q890 steel plate for a hydraulic bracket meeting the welding heat input of 30kJ/cm comprises the following steps:
(1) smelting molten steel according to set components and casting the molten steel into a casting blank, wherein the thickness of the casting blank is 250 mm;
(2) heating the casting blank to 1180-1220 ℃, and carrying out 5-7 passes of rolling in the first stage, wherein the initial rolling temperature is 1080-1150 ℃, and the final rolling temperature is 980-1070 ℃, so as to obtain an intermediate blank with the thickness of 70-100 mm;
(3) the intermediate blank is heated to 950-1000 ℃, 5-7 passes of rolling are carried out in the second stage, the final rolling temperature is 850-880 ℃, the reduction amount of each pass is controlled to be 15-20%, and the thickness of the steel plate after final rolling is 20-30 mm;
(4) after finishing rolling, cooling the steel plate to 200 ℃ at the speed of 30-50 ℃/s, and then placing the steel plate on a cooling bed to cool to room temperature;
(5) and (3) performing off-line tempering on the steel plate at 400 ℃, wherein the tempering time is 1 h.
The invention mainly solves the problem that the toughness and the strength of a heat affected zone of experimental steel are reduced under the condition of a high-heat input welding process, Zr element capable of inducing high-strength and high-toughness bainite in coarse austenite grains is added in the component design, meanwhile, the austenite grain size is refined through Ti, a certain amount of Mo and V elements are added to inhibit the softening behavior of a welded structure, and finally, the mechanical property of the steel meets the Q890, and the steel still has good comprehensive use performance under the condition that the welding heat input value reaches 30 kJ/cm.
The steel plate composition of the invention takes the following points into consideration:
1) carbon is effective for strengthening steel sheets, but at the same time, it reduces formability and weldability of steel sheets, which are essential for their use properties, and therefore, the content of carbon is controlled within a range of low carbon steel;
2) manganese can effectively improve the performance of steel through solid solution strengthening and phase transformation strengthening, but too high manganese can generate component segregation and influence the low-temperature toughness of a final product, so that the content of manganese is controlled to be about 1.5 percent;
3) molybdenum and vanadium are important elements in the invention, wherein the hardenability of the steel plate can be obviously improved after the molybdenum element is added, so that the steel plate can obtain a high-strength martensite structure, and meanwhile, the molybdenum and vanadium are added in a composite manner, so that the softening of the structure of a welding heat affected zone in the welding process can be effectively inhibited, and the welding part still has high strength value under the condition of high welding heat input;
4) zirconium is one of important elements in the invention, and is matched with trace titanium element, so that the structure nucleation in coarse austenite grains can be effectively promoted, the nucleation structure is mainly high-strength and high-toughness acicular ferrite and bainite, and the requirement of high toughness of a welding heat affected zone under the condition of higher heat input can be met;
5) boron is one of important elements in the invention, the addition of boron into steel can obviously improve the critical cooling rate of the steel plate to obtain martensite or bainite, and the addition of trace boron can improve the critical cooling rate of steel by more than 3 times, thereby ensuring that the steel plate under the alloy system can obtain martensite structure. When the boron content is more than 5ppm in terms of the amount of boron added, the effect of hardenability is remarkable, but too much boron forms brittle BN precipitates with nitrogen, grain boundary strength is reduced, and low temperature toughness of the steel sheet is remarkably reduced, so that a good toughness effect can be obtained by controlling the amount of boron to be 6 to 10 ppm.
Compared with the prior low-alloy high-strength steel with the same strength grade, the Q890 steel plate has the following advantages: the welding heat input energy can be larger while the same mechanical property requirement is met, and the welding heat input energy has better comprehensive use performance, especially welding use performance. Meanwhile, under the condition of higher welding heat input, the welding efficiency is higher, the production efficiency can be obviously improved, and a feasible route is provided for batch production and use of the steel for the hydraulic support with higher strength grade.
Drawings
FIG. 1 is an optical micrograph of a steel sheet prepared in example 1 of the present invention.
Detailed Description
The present invention will be described in further detail with reference to examples.
The steel plate of the embodiment of the invention has the components shown in the table 1, and the preparation process flow of the steel plate of the embodiment of the invention is as follows: converter smelting → LF → RH → casting blank heating → hot rolling → cooling → off-line tempering, wherein the casting blank heating: 1180-1220 ℃, the rolling start temperature of the first stage is 1080-1150 ℃, the final rolling temperature is 980-1070 ℃, and an intermediate blank with the thickness of 70-100 mm is obtained; the intermediate blank is heated to 950-1000 ℃, the final rolling temperature of the second stage is 850-880 ℃, the reduction amount of each pass is controlled to be 15-20%, and the thickness of the steel plate after final rolling is 20-30 mm; after finishing rolling, cooling the steel plate to 200 ℃ at the speed of 30-50 ℃/s, and then placing the steel plate on a cooling bed to cool to room temperature; and (3) performing off-line tempering on the steel plate at 400 ℃, wherein the tempering time is 1 h.
The preparation process parameters of the steel plates of the embodiments of the invention are shown in Table 2, the mechanical properties of the steel plates prepared in the embodiments 1-3 of the invention are shown in Table 3, and the welding properties of the steel plates prepared in the embodiments 1-3 of the invention are shown in Table 4.
The process flow of the embodiment of the invention is as follows:
table 1 steel sheet compositions/weight percentages of examples 1-3
| Examples | C | Si | Mn | P | S | Mo | V | Zr | Ti | B |
| 1 | 0.12 | 0.35 | 1.5 | 0.008 | 0.005 | 0.50 | 0.08 | 0.02 | 0.02 | 0.0006 |
| 2 | 0.13 | 0.30 | 1.6 | 0.009 | 0.004 | 0.60 | 0.08 | 0.03 | 0.02 | 0.0008 |
| 3 | 0.12 | 0.33 | 1.5 | 0.010 | 0.004 | 0.55 | 0.09 | 0.02 | 0.03 | 0.0010 |
TABLE 2 Hot Rolling Process parameters for Steel plates of examples 1-3 and thickness of the corresponding products
Note: the tempering temperature of examples 1 to 3 was 400 ℃ and the tempering time was 1 hour.
Table 3 thickness of steel sheets of examples 1-3 and corresponding mechanical properties
As shown in Table 3, the thickness of the steel plate is 20-30mm, the yield strength reaches 920-940MPa, the tensile strength reaches 1008-1020MPa, the elongation is 16.0-16.5%, and the impact energy at-20 ℃ is 180-210J, so that the requirement on the mechanical property of the Q890 steel plate is met.
TABLE 4 mechanical Properties of weld joints of the steel sheets of examples 1-3 under welding Heat input
As shown in Table 4, the thickness of the steel plate is 20-30mm, when a welding heat input value of 30kJ/cm is adopted, the tensile strength of a welding joint is 990-1010MPa, the low-temperature impact energy of the center of the welding line, the fusion line and the outside of the fusion line all meet the requirements of a welding test, and the fracture position of the welding joint is in the center of the welding line, which indicates that the steel plate has good welding performance under the welding process condition of 30 kJ/cm.
Although embodiments of the present invention have been shown and described, it will be appreciated by those skilled in the art that changes, modifications, substitutions and alterations can be made in these embodiments without departing from the principles and spirit of the invention, the scope of which is defined in the appended claims and their equivalents.
Claims (1)
1. A Q890 steel plate for a hydraulic support meeting the welding heat input of 30kJ/cm is characterized by comprising the following chemical components in percentage by weight: 0.12-0.13% of C, 0.30-0.35% of Si, 1.5-1.6% of Mn, 0.008-0.010% of P, 0.004-0.005% of S, 0.5-0.6% of Mo, 0.08-0.09% of V, 0.0006-0.0010% of B, 0.02-0.03% of Zr, 0.02-0.03% of Ti, and the balance of Fe and inevitable impurities;
the thickness of the steel plate is 20-30mm, the yield strength reaches 900MPa, the tensile strength reaches 1000MPa, the elongation after fracture is 16%, the impact energy at minus 20 ℃ is 200J, and the welding heat input reaches 30 kJ/cm;
the preparation method of the Q890 steel plate for the hydraulic support meeting the welding heat input of 30kJ/cm comprises the following steps:
(1) smelting molten steel according to set components and casting the molten steel into a casting blank, wherein the thickness of the casting blank is 250 mm;
(2) heating the casting blank to 1180-1220 ℃, and carrying out 5-7 passes of rolling in the first stage, wherein the initial rolling temperature is 1080-1150 ℃, and the final rolling temperature is 980-1070 ℃, so as to obtain an intermediate blank with the thickness of 70-100 mm;
(3) the intermediate blank is heated to 950-1000 ℃, 5-7 passes of rolling are carried out in the second stage, the final rolling temperature is 850-880 ℃, the reduction amount of each pass is controlled to be 15-20%, and the thickness of the steel plate after final rolling is 20-30 mm;
(4) after finishing rolling, cooling the steel plate to 200 ℃ at the speed of 30-50 ℃/s, and then placing the steel plate on a cooling bed to cool to room temperature;
(5) and (3) performing off-line tempering on the steel plate at 400 ℃, wherein the tempering time is 1 h.
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Citations (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102162061A (en) * | 2010-02-23 | 2011-08-24 | 宝山钢铁股份有限公司 | Low-carbon bainite thick steel plate with high strength and toughness and manufacturing method thereof |
| CN102268607A (en) * | 2010-06-07 | 2011-12-07 | 鞍钢股份有限公司 | High-strength and high-toughness steel plate special for coal mine hydraulic support and manufacturing method thereof |
| CN103320717A (en) * | 2013-06-04 | 2013-09-25 | 南京钢铁股份有限公司 | Ultra high-strength high titanium steel plate with yield strength of 960 MPa and preparing method of same |
| CN103555911A (en) * | 2013-11-12 | 2014-02-05 | 湖南华菱湘潭钢铁有限公司 | Production method of quenched and tempered high-strength Q890E super-thick steel plate |
| CN103589969A (en) * | 2013-11-12 | 2014-02-19 | 湖南华菱湘潭钢铁有限公司 | Production method of quenched and tempered high-intensity Q890D super-thick steel plate |
| CN105063497A (en) * | 2015-09-17 | 2015-11-18 | 东北大学 | High-wear-resistance high-machinability low-alloy wear-resistant steel plate and manufacturing method thereof |
| CN105880834A (en) * | 2016-05-18 | 2016-08-24 | 太原科技大学 | Welding method of Q890 high-strength steel |
| CN106148822A (en) * | 2016-08-23 | 2016-11-23 | 南京钢铁股份有限公司 | A kind of press quenching produces the method for high-strength steel Q890 cut deal |
| CN109266812A (en) * | 2018-10-10 | 2019-01-25 | 安阳钢铁股份有限公司 | A kind of coal mine hydraulic supporting low yield strength ratio high-strength hardened and tempered steel and its manufacturing method |
| CN109576568A (en) * | 2017-09-28 | 2019-04-05 | 宝山钢铁股份有限公司 | A kind of high-strength weldable casing and its manufacturing method |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP4279231B2 (en) * | 2004-10-22 | 2009-06-17 | 株式会社神戸製鋼所 | High-strength steel material with excellent toughness in weld heat affected zone |
| WO2018079026A1 (en) * | 2016-10-27 | 2018-05-03 | Ｊｆｅスチール株式会社 | Steel for high heat input welding |
-
2020
- 2020-08-07 CN CN202010786319.7A patent/CN111910127B/en active Active
Patent Citations (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102162061A (en) * | 2010-02-23 | 2011-08-24 | 宝山钢铁股份有限公司 | Low-carbon bainite thick steel plate with high strength and toughness and manufacturing method thereof |
| CN102268607A (en) * | 2010-06-07 | 2011-12-07 | 鞍钢股份有限公司 | High-strength and high-toughness steel plate special for coal mine hydraulic support and manufacturing method thereof |
| CN103320717A (en) * | 2013-06-04 | 2013-09-25 | 南京钢铁股份有限公司 | Ultra high-strength high titanium steel plate with yield strength of 960 MPa and preparing method of same |
| CN103555911A (en) * | 2013-11-12 | 2014-02-05 | 湖南华菱湘潭钢铁有限公司 | Production method of quenched and tempered high-strength Q890E super-thick steel plate |
| CN103589969A (en) * | 2013-11-12 | 2014-02-19 | 湖南华菱湘潭钢铁有限公司 | Production method of quenched and tempered high-intensity Q890D super-thick steel plate |
| CN105063497A (en) * | 2015-09-17 | 2015-11-18 | 东北大学 | High-wear-resistance high-machinability low-alloy wear-resistant steel plate and manufacturing method thereof |
| CN105880834A (en) * | 2016-05-18 | 2016-08-24 | 太原科技大学 | Welding method of Q890 high-strength steel |
| CN106148822A (en) * | 2016-08-23 | 2016-11-23 | 南京钢铁股份有限公司 | A kind of press quenching produces the method for high-strength steel Q890 cut deal |
| CN109576568A (en) * | 2017-09-28 | 2019-04-05 | 宝山钢铁股份有限公司 | A kind of high-strength weldable casing and its manufacturing method |
| CN109266812A (en) * | 2018-10-10 | 2019-01-25 | 安阳钢铁股份有限公司 | A kind of coal mine hydraulic supporting low yield strength ratio high-strength hardened and tempered steel and its manufacturing method |
Non-Patent Citations (4)
| Title |
|---|
| Q890高强度结构钢在液压支架应用的试验研究;徐亚军等;《煤矿开采》;20160615;第21卷(第03期);46-48 * |
| 包钢Q890D高强钢的研制;黄楠等;《包钢科技》;20170225;第43卷(第01期);37-39 * |
| 热输入对Q890D低合金高强钢焊接性能的影响;韩振仙， 兰志宇等;《焊接生产应用》;20191231(第3期);56-64 * |
| 焊接热输入对 Q890 高强钢热影响区裂纹扩展的影响;崔冰、彭云等;《焊接学报》;20170831;第38卷(第8期);63-67 * |
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