CN114635083A - Method for improving low-temperature impact toughness of steel plate core of ultra-thick 15CrMoR pressure vessel - Google Patents
Method for improving low-temperature impact toughness of steel plate core of ultra-thick 15CrMoR pressure vessel Download PDFInfo
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- CN114635083A CN114635083A CN202210208555.XA CN202210208555A CN114635083A CN 114635083 A CN114635083 A CN 114635083A CN 202210208555 A CN202210208555 A CN 202210208555A CN 114635083 A CN114635083 A CN 114635083A
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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
- 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
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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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
- 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
- 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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- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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Abstract
The invention discloses a method for improving the low-temperature impact toughness of the core of a 15CrMoR pressure vessel steel plate with an ultra-thick specification, which greatly improves the low-temperature impact toughness of the core of the 15CrMoR pressure vessel steel plate with the ultra-thick specification through a heat treatment method of sub-warm quenching and high-temperature tempering, stably controls the low-temperature impact work of the core of the 15CrMoR pressure vessel steel plate with the thickness of more than 60mm to be more than 100J at the temperature of minus 20 ℃, ensures that other properties of the steel plate all meet the standard requirements, and obviously improves the qualification rate of the thick steel plate.
Description
Technical Field
The invention relates to the technical field of metallurgy, in particular to a method for improving the low-temperature impact toughness of the core part of a super-thick 15CrMoR pressure vessel steel plate.
Background
The 15CrMoR is steel for a pressure container in GB/T713-2014 and GB/T35012-2018, requires normalization and tempering for delivery according to standards, is widely applied to petrochemical industry and coal chemical industry, is used for manufacturing hydrogenation reactors, reduction reactors, transformation furnaces, gasification furnaces, heat exchangers, towers, thermal high-pressure separators, dephlegmators and other equipment, and requires a steel plate to have high-temperature strength and plastic shape, good low-temperature impact toughness, excellent oxidation resistance and corrosion resistance, good processing performance and welding performance and good tissue stability under the condition of severe service environment (high temperature and high pressure at 400 ℃, hydrogen corrosion and long-time tempering embrittlement). High technical requirement and high production difficulty.
In the aspect of low-temperature impact toughness, the impact energy at 1/4 and 1/2 thicknesses at-20 ℃ is generally required to be qualified, and production practices show that the impact energy at 1/4 and 1/2 thicknesses at-20 ℃ of a steel plate with the thickness of less than 60mm is stable, but the low-temperature impact energy is usually greatly reduced when the steel plate with the thickness of more than 60mm is produced by adopting the traditional normalizing and tempering process, and particularly the impact energy at 1/2 thickness cannot meet the standard requirement, so that the steel plate is unqualified, and further loss is brought to enterprises. Therefore, the improvement of the low-temperature impact toughness of the ultra-thick steel plate becomes a technical difficulty and innovation point for developing and producing the steel for the 15CrMoR pressure vessel.
Patent CN107760987A discloses a 15CrMoR steel plate and a method for improving the low-temperature impact toughness of the core thereof, and the heat treatment method of the normalizing and tempering process improves the low-temperature impact toughness of the core of the 15CrMoR steel plate with thick specification by preheating treatment before normalizing. The method has the defects that the method is only suitable for 15CrMoR steel plates, is not suitable for other steel plates and increases the production cost.
Patent CN101876001A discloses a method for improving low-temperature impact toughness of a high-strength thick steel plate, which adopts a heat treatment process of quenching + tempering to control the structure of the steel plate after secondary quenching to be a mixed structure of hard phase and soft phase, thereby improving the low-temperature toughness of the steel plate. The defects that the production cost is obviously increased by adopting two times of quenching;
patent CN105420468A discloses a heat treatment method for ensuring low-temperature toughness of thick high-strength steel, which improves the low-temperature toughness of the thick high-strength steel through heat treatment methods of quenching, tempering and secondary tempering. The defects that the method is only suitable for the steel grade, twice tempering is adopted, and the production cost is obviously increased.
Disclosure of Invention
The invention aims to provide a method for improving the low-temperature impact toughness of the core part of a 15CrMoR pressure vessel steel plate with an ultra-thick specification, which greatly improves the low-temperature impact toughness of the core part of the 15CrMoR pressure vessel steel plate with the ultra-thick specification, stably controls the core low-temperature impact energy of the 15CrMoR pressure vessel steel plate with the thickness of more than 60mm to be more than 100J at the temperature of minus 20 ℃, and obviously improves the qualification rate of the thick steel plate.
In order to solve the technical problems, the invention adopts the following technical scheme:
the invention relates to a method for improving the low-temperature impact toughness of the core part of a 15CrMoR pressure vessel steel plate with an ultra-thick specification, which comprises the following steps of molten iron pretreatment, converter smelting, LF refining, RH vacuum treatment, continuous casting, slab slow cooling, slab heating, high-pressure water dephosphorization, rough rolling, finish rolling, Acc cooling and heat treatment after the Acc cooling, wherein the heat treatment comprises sub-temperature quenching and high-temperature tempering, the quenching heating temperature of the sub-temperature quenching is an austenite-ferrite two-phase region, the temperature is 830-870 ℃, the in-furnace time is 1.4min/mm multiplied by t (mm) + 10-20 min, t is the thickness of the steel plate, and the steel plate is quenched to the room temperature after being taken out of the furnace; the tempering temperature of the high-temperature tempering is 680-720 ℃, the furnace time is 2.3min/mm x t (mm) + 30-40 min, and t is the thickness of the steel plate.
Further, the steel plate comprises the following chemical components in percentage by weight: 0.15 to 0.17%, Si: 0.25 to 0.35%, Mn: 0.52-0.69%, P: less than or equal to 0.009%, S: less than or equal to 0.004%, 1.06-1.15% of Cr, 0.50-0.59% of Mo, less than or equal to 0.003% of Sb, less than or equal to 0.010% of Sn, less than or equal to 0.010% of As, less than or equal to 150% of J coefficient, less than or equal to 15% of X coefficient, and the balance of Fe and inevitable impurities.
Further, the thickness of the steel plate is 65mm, the steel plate is subjected to heat treatment after shot blasting, the quenching heating temperature is 850 ℃, the furnace time is 94 minutes, the steel plate is quenched to the room temperature after being taken out of the furnace, then the tempering treatment is carried out, the tempering temperature is 700 ℃, the furnace time is 168 minutes, and the steel plate is air-cooled after being taken out of the furnace.
Further, the thickness of the steel plate is 70mm, the steel plate is subjected to heat treatment after shot blasting, the quenching heating temperature is 850 ℃, the furnace time is 108 minutes, the steel plate is quenched to the room temperature after being taken out of the furnace, then the tempering treatment is carried out, the tempering temperature is 700 ℃, the furnace time is 191 minutes, and the steel plate is taken out of the furnace and then is subjected to air cooling.
Further, the thickness of the steel plate is 75mm, the steel plate is subjected to heat treatment after shot blasting, the quenching heating temperature is 850 ℃, the furnace time is 115 minutes, the steel plate is quenched to the room temperature after being taken out of the furnace, then the tempering treatment is carried out, the tempering temperature is 700 ℃, the furnace time is 202 minutes, and the steel plate is air-cooled after being taken out of the furnace.
Compared with the prior art, the invention has the beneficial technical effects that:
(1) through a heat treatment method of sub-temperature quenching and high-temperature tempering, the low-temperature impact toughness of the core of the ultra-thick 15CrMoR pressure vessel steel plate is greatly improved, the-20 ℃ core low-temperature impact energy of the 15CrMoR pressure vessel steel plate with the thickness of more than 60mm is stably controlled to be more than 100J, other properties of the steel plate meet standard requirements, and the qualification rate of the thick steel plate is remarkably improved.
(2) The method creates conditions for stably producing the steel plate of the super-thick pressure vessel by adopting the continuous casting slab with the thickness of 250-300 mm. Through actual production and inspection, the mechanical property is excellent, and the technical difficulty of thick container steel production is solved.
Drawings
The invention is further illustrated in the following description with reference to the drawings.
FIG. 1 shows the metallographic structure of a steel sheet according to example 1 of the present invention.
Detailed Description
The present invention is described in more detail below with reference to examples. These examples are merely illustrative of the best mode of carrying out the invention and do not limit the scope of the invention in any way.
Example 1
The chemical composition of the 15CrMoR pressure vessel steel of example 1 is shown in table 1. The production process comprises the steps of molten iron pretreatment, converter smelting, LF refining, RH vacuum treatment, continuous casting, slab slow cooling, slab heating, high-pressure water dephosphorization, rough rolling, finish rolling, Acc cooling and steel plate thickness of 65 mm. And performing heat treatment on the steel plate after shot blasting, wherein the quenching heating temperature is 850 ℃, the furnace time is 94 minutes, and the steel plate is quenched to room temperature after being taken out of the furnace. And then tempering treatment is carried out, the tempering temperature is 700 ℃, the furnace time is 168 minutes, and air cooling is carried out after discharging. The properties of the steel sheet are shown in Table 2.
Example 2
The implementation mode is the same as example 1, and the production process route comprises molten iron pretreatment, converter smelting, LF refining, RH vacuum treatment, continuous casting, slab slow cooling, slab heating, high-pressure water dephosphorization, rough rolling, finish rolling and Acc cooling, wherein the thickness of a steel plate is 70 mm. And performing heat treatment on the steel plate after shot blasting, wherein the quenching heating temperature is 850 ℃, the in-furnace time is 108 minutes, and the steel plate is taken out of the furnace and then quenched to room temperature. And then tempering treatment is carried out, the tempering temperature is 700 ℃, the furnace time is 191 minutes, and air cooling is carried out after discharging. The properties of the steel sheet are shown in Table 2.
Example 3
The implementation mode is the same as example 1, and the production process route comprises the steps of molten iron pretreatment, converter smelting, LF refining, RH vacuum treatment, continuous casting, slab slow cooling, slab heating, high-pressure water dephosphorization, rough rolling, finish rolling and Acc cooling, wherein the thickness of a steel plate is 75 mm. And performing heat treatment on the steel plate after shot blasting, wherein the quenching heating temperature is 850 ℃, the in-furnace time is 115 minutes, and the steel plate is taken out of the furnace and then quenched to room temperature. And then tempering treatment is carried out, wherein the tempering temperature is 700 ℃, the furnace time is 202 minutes, and air cooling is carried out after discharging. The properties of the steel sheet are shown in Table 2.
TABLE 1 chemical composition (wt%) of inventive examples 1 to 3
| Examples | C | Si | Mn | P | S | Cr | Mo | Sb | Sn | As | J | X |
| 1 | 0.155 | 0.25 | 0.59 | 0.008 | 0.002 | 1.10 | 0.55 | 0.0001 | 0.0013 | 0.0018 | 126 | 13.5 |
| 2 | 0.161 | 0.26 | 0.60 | 0.007 | 0.001 | 1.08 | 0.54 | 0.0001 | 0.0016 | 0.0018 | 127 | 13.6 |
| 3 | 0.153 | 0.28 | 0.56 | 0.007 | 0.002 | 1.05 | 0.56 | 0.0001 | 0.0015 | 0.0020 | 128 | 13.7 |
The steel plates of inventive examples 1-3 were tested for conventional mechanical properties, impact properties, and bending properties, and the results are shown in table 2.
TABLE 2 mechanical properties of the steel sheets of examples 1 to 3 of the present invention
As can be seen from Table 2, the comparative examples are the properties of the steel sheets after the conventional normalizing + tempering heat treatment method, and the steel sheets have failed to meet the standard requirements because the steel sheets have too large thickness and small compression ratio, and the impact properties at 1/2 thickness at-20 ℃ are deteriorated and the impact energy is unstable. Examples 1-3 show that the performance of the steel plate after the invention is adopted, the impact performance at-20 ℃ of 1/2 thickness and the stability thereof are obviously improved, and the technical difficulty of producing the ultra-thick 15CrMoR pressure vessel steel with the thickness of more than 60mm is solved.
The above-mentioned embodiments are only for describing the preferred mode of the present invention, and do not limit the scope of the present invention, and various modifications and improvements made to the technical solution of the present invention by those skilled in the art without departing from the spirit of the present invention should fall within the protection scope defined by the claims of the present invention.
Claims (5)
1. A method for improving the low-temperature impact toughness of the core part of a 15CrMoR pressure vessel with an ultra-thick specification comprises the following steps of molten iron pretreatment, converter smelting, LF refining, RH vacuum treatment, continuous casting, slab slow cooling, slab heating, high-pressure water dephosphorization, rough rolling, finish rolling and Acc cooling, and is characterized by further comprising the steps of performing heat treatment after Acc cooling, wherein the heat treatment comprises sub-temperature quenching and high-temperature tempering, the quenching heating temperature of the sub-temperature quenching is an austenite-ferrite two-phase region, the temperature is 830-870 ℃, the furnace time is 1.4min/mm multiplied by t (mm) + 10-20 min, t is the thickness of a steel plate, and the steel plate is quenched to the room temperature after being taken out of the furnace; the tempering temperature of the high-temperature tempering is 680-720 ℃, the furnace time is 2.3min/mm x t (mm) + (30-40 min), and t is the thickness of the steel plate.
2. The method for improving the low-temperature impact toughness of the core part of the ultra-thick 15CrMoR pressure vessel steel plate according to claim 1, wherein the steel plate comprises the following chemical components in percentage by weight: 0.15 to 0.17%, Si: 0.25 to 0.35%, Mn: 0.52-0.69%, P: less than or equal to 0.009%, S: less than or equal to 0.004%, 1.06-1.15% of Cr, 0.50-0.59% of Mo, less than or equal to 0.003% of Sb, less than or equal to 0.010% of Sn, less than or equal to 0.010% of As, less than or equal to 150% of J coefficient, less than or equal to 15% of X coefficient, and the balance of Fe and inevitable impurities.
3. The method for improving the low-temperature impact toughness of the core part of the steel plate of the ultra-thick 15CrMoR pressure vessel as claimed in claim 2, wherein the thickness of the steel plate is 65mm, the steel plate is subjected to heat treatment after shot blasting, the quenching heating temperature is 850 ℃, the furnace time is 94 minutes, the steel plate is taken out of the furnace and then quenched to the room temperature, then the tempering treatment is carried out, the tempering temperature is 700 ℃, the furnace time is 168 minutes, and the steel plate is taken out of the furnace and then air-cooled.
4. The method for improving the low-temperature impact toughness of the core part of the steel plate of the ultra-thick 15CrMoR pressure vessel as claimed in claim 2, wherein the thickness of the steel plate is 70mm, the steel plate is subjected to heat treatment after shot blasting, the quenching heating temperature is 850 ℃, the furnace time is 108 minutes, the steel plate is taken out of the furnace and then quenched to room temperature, and then the tempering treatment is carried out, the tempering temperature is 700 ℃, the furnace time is 191 minutes, and the steel plate is taken out of the furnace and then air-cooled.
5. The method for improving the low-temperature impact toughness of the core part of the steel plate of the ultra-thick 15CrMoR pressure vessel as claimed in claim 2, wherein the steel plate is 75mm thick, the steel plate is subjected to heat treatment after being shot-blasted, the quenching heating temperature is 850 ℃, the furnace time is 115 minutes, the steel plate is taken out of the furnace and then is quenched to room temperature, then the tempering treatment is carried out, the tempering temperature is 700 ℃, the furnace time is 202 minutes, and the steel plate is taken out of the furnace and then is air-cooled.
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Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2005008931A (en) * | 2003-06-18 | 2005-01-13 | Sumitomo Metal Ind Ltd | Steel material suitable for large heat input welding for steel frame |
| CN104805380A (en) * | 2015-05-06 | 2015-07-29 | 山东钢铁股份有限公司 | Low-temper-brittleness Cr-Mo steel plate for high temperature resisting pressure-bearing equipment and preparation method of steel plate |
| CN107760987A (en) * | 2017-09-20 | 2018-03-06 | 舞阳钢铁有限责任公司 | 15CrMoR steel plates and its method for improving center portion low-temperature impact toughness |
| CN109518079A (en) * | 2018-11-22 | 2019-03-26 | 湖南华菱湘潭钢铁有限公司 | A kind of production method of hydrogen-contacting equipment 15CrMoR steel plate |
| CN111926244A (en) * | 2020-07-09 | 2020-11-13 | 舞阳钢铁有限责任公司 | 15CrMoR steel plate with good low-temperature impact toughness and production method thereof |
| KR20210000844A (en) * | 2019-06-26 | 2021-01-06 | 현대제철 주식회사 | Pressure vessel steel sheet excellent in pwhthresistance and menufacturing mwthod thereof |
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- 2022-03-04 CN CN202210208555.XA patent/CN114635083A/en active Pending
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2005008931A (en) * | 2003-06-18 | 2005-01-13 | Sumitomo Metal Ind Ltd | Steel material suitable for large heat input welding for steel frame |
| CN104805380A (en) * | 2015-05-06 | 2015-07-29 | 山东钢铁股份有限公司 | Low-temper-brittleness Cr-Mo steel plate for high temperature resisting pressure-bearing equipment and preparation method of steel plate |
| CN107760987A (en) * | 2017-09-20 | 2018-03-06 | 舞阳钢铁有限责任公司 | 15CrMoR steel plates and its method for improving center portion low-temperature impact toughness |
| CN109518079A (en) * | 2018-11-22 | 2019-03-26 | 湖南华菱湘潭钢铁有限公司 | A kind of production method of hydrogen-contacting equipment 15CrMoR steel plate |
| KR20210000844A (en) * | 2019-06-26 | 2021-01-06 | 현대제철 주식회사 | Pressure vessel steel sheet excellent in pwhthresistance and menufacturing mwthod thereof |
| CN111926244A (en) * | 2020-07-09 | 2020-11-13 | 舞阳钢铁有限责任公司 | 15CrMoR steel plate with good low-temperature impact toughness and production method thereof |
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