CN114346194A - Q1100D ultrahigh-strength steel casting method - Google Patents
Q1100D ultrahigh-strength steel casting method Download PDFInfo
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- CN114346194A CN114346194A CN202111546160.2A CN202111546160A CN114346194A CN 114346194 A CN114346194 A CN 114346194A CN 202111546160 A CN202111546160 A CN 202111546160A CN 114346194 A CN114346194 A CN 114346194A
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- 238000005266 casting Methods 0.000 title claims abstract description 70
- 229910000797 Ultra-high-strength steel Inorganic materials 0.000 title claims abstract description 22
- 238000000034 method Methods 0.000 title claims abstract description 12
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 32
- 239000010959 steel Substances 0.000 claims abstract description 32
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 17
- 239000002893 slag Substances 0.000 claims description 10
- 230000009467 reduction Effects 0.000 claims description 9
- 238000010583 slow cooling Methods 0.000 claims description 7
- 230000004907 flux Effects 0.000 claims description 6
- 238000003756 stirring Methods 0.000 claims description 6
- 238000001816 cooling Methods 0.000 claims description 5
- 239000000498 cooling water Substances 0.000 claims description 5
- 238000010438 heat treatment Methods 0.000 claims description 5
- 239000011572 manganese Substances 0.000 claims description 5
- 238000002844 melting Methods 0.000 claims description 5
- 230000008018 melting Effects 0.000 claims description 5
- 229910052799 carbon Inorganic materials 0.000 claims description 4
- 229910052748 manganese Inorganic materials 0.000 claims description 4
- 229910045601 alloy Inorganic materials 0.000 claims description 3
- 239000000956 alloy Substances 0.000 claims description 3
- 239000012535 impurity Substances 0.000 claims description 3
- 239000007788 liquid Substances 0.000 claims description 3
- 239000000126 substance Substances 0.000 claims description 3
- 229910052804 chromium Inorganic materials 0.000 claims description 2
- 229910052750 molybdenum Inorganic materials 0.000 claims description 2
- 229910052759 nickel Inorganic materials 0.000 claims description 2
- 229910052758 niobium Inorganic materials 0.000 claims description 2
- 229910052720 vanadium Inorganic materials 0.000 claims description 2
- 238000005204 segregation Methods 0.000 abstract description 8
- 238000005096 rolling process Methods 0.000 description 4
- 230000000694 effects Effects 0.000 description 3
- 230000006872 improvement Effects 0.000 description 3
- 238000004519 manufacturing process Methods 0.000 description 3
- 230000009286 beneficial effect Effects 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 230000008569 process Effects 0.000 description 2
- 210000000988 bone and bone Anatomy 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
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Abstract
The invention discloses a method for casting Q1100D ultrahigh-strength steel, which focuses on adopting technical measures from a casting machine to avoid surface cracks of an ultrahigh-strength steel casting blank, improves the central segregation control level of the ultrahigh-strength steel casting blank and achieves the purpose of ensuring all performances of the casting blank to be qualified after being rolled into a steel plate.
Description
Technical Field
The invention relates to the technical field of continuous casting in the metallurgical industry, in particular to a Q1100D ultrahigh-strength steel casting method.
Background
With the continuous development of the mechanical industry towards large-scale and light-weight, more and more high-strength steel and ultrahigh-strength steel are used in large quantities, the ultrahigh-strength steel with the yield strength of 1100MP is the steel grade with the highest strength level in the field of current domestic engineering machinery, and the ultrahigh-strength steel is mainly used for key components of middle arms of concrete pump trucks and automobile cranes in the engineering machinery industry in the expansion period, crawler crane bases and pull plates, large-tonnage hydraulic supports and the like. Because of the special properties of high yield strength, high straightness and the like, the steel industry at home and abroad is always called as 'hard bone' in high-strength steel, only a few steel industries can produce the steel grade at present, and a large amount of foreign exchange is imported from developed countries every year.
The difficulty of ultrahigh-strength steel production is mainly that due to high alloy content, a casting blank is easy to generate surface cracks during casting, the strength stability of the casting blank is difficult to master, and the subsequent rolling and heat treatment processes can be partially overcome by taking measures, but the premise is that a casting machine must cast qualified slabs, the surface quality of the slabs is required to be good, no obvious center segregation exists in the slabs, and the low-power rating reaches more than C1.0.
Many studies on the production of ultra-high strength steel are being made, but most of the studies are focused on improving the strength stability of the ultra-high strength steel through rolling and heat treatment processes, for example, chinese patent No. 202010246571.9 discloses a method for producing a Q1100D/E ultra-thin steel plate for a high strength structure, which focuses on ensuring the toughness, weldability and straightness of the steel plate by taking technical measures from the aspects of rolling and heat treatment. But does not describe the improvement of the surface quality of the ultra-high strength steel plate and the improvement of the control level of the center segregation of the ultra-high strength steel casting blank from the casting angle of the casting machine.
Disclosure of Invention
In order to solve the technical problems, the invention aims to provide a Q1100D ultrahigh-strength steel casting method, which focuses on adopting technical measures from a casting machine to avoid surface cracks of an ultrahigh-strength steel casting blank, improves the central segregation control level of the ultrahigh-strength steel casting blank, and achieves the purpose of ensuring that all performances of the casting blank are qualified after being rolled into a steel plate.
In order to solve the technical problems, the invention adopts the following technical scheme:
the invention discloses a Q1100D ultrahigh-strength steel casting method, which comprises the following steps:
(1) the Q1100D high-strength steel comprises the following chemical components in percentage by mass:
0.16 percent of C, 0.2 percent of Si, 1.15 percent of Mn, less than or equal to 0.008 percent of P, less than or equal to 0.002 percent of S, 0.027 percent of Alt, 0.025 percent of Als, 0.025 percent of Nb, 0.055 percent of V, 0.02 percent of Ti, 0.25 percent of Cr, 0.6 percent of Mo, 0.35 percent of Ni, 0.0017 percent of Ca, 0.0015 percent of B, and the balance of Fe and inevitable impurities;
(3) the casting section adopts a 2000 multiplied by 250 section;
(3) in order to ensure the surface quality of a casting blank, the technical measures adopted comprise:
A. the water quantity of the crystallizer is 4300L/min, the water quantity of the narrow side is 370L/min, and the water temperature of the crystallizer is 35-38 ℃;
B. the temperature of the secondary cooling water is stabilized at 28 ℃, and the specific water amount is 0.80L/kg steel;
C. the casting pulling speed is stabilized at 1.0 m/min;
D. medium-carbon high-manganese low-alloy type covering slag is used as the crystallizer covering slag, the viscosity is required to be 0.7-1.2Pa.s, and the melting point is 1100-1150 ℃;
E. before casting, checking the radian and the opening degree of the sector section, wherein the radian error is required to be less than or equal to 0.3 mm; the error of the opening degree is less than or equal to 1 mm;
(4) in order to ensure the internal quality of a casting blank, the technical measures adopted comprise:
A. controlling the superheat degree of molten steel at 15-25 ℃ during casting;
B. adopting secondary cooling electromagnetic stirring, and respectively installing a double-roller type mixer at the outlet of the sector 3 section and the inlet of the sector 4 section, wherein the current is 330A, and the frequency is 5 Hz;
C. the soft reduction adopts three sections of sector 8, sector 9 and sector 10 for reduction, and the reduction amounts are respectively 3.3mm, 3.3mm and 1.5 mm;
(5) and (3) after casting a casting blank, not carrying out hot charging, and taking the casting blank off the line to a slow cooling pit with a heating function in a slow cooling mode for more than 72 hours.
Further, the furnace 1 is arranged with other lower grade steel grade during casting, and the Q1100D steel grade is arranged after the water temperature is stable after the furnace 2.
Further, the mold flux used was a model YK2P-3 of sinoislando starbo, which had a viscosity of 0.77pa.s and a melting point of 1141 ℃.
Furthermore, the liquid slag layer is measured to be 12mm during casting, and the slag consumption is measured to be 0.46 kg/ton steel.
Compared with the prior art, the invention has the beneficial technical effects that:
(1) the casting blank has good surface quality, shallow vibration mark and no surface crack, and the surface quality is good after the steel plate is rolled.
(2) The casting blank has good internal quality and light center segregation, the low-power result can reach more than C1.0, and no middle crack or center crack exists.
(3) The optimized use of the electromagnetic stirring in the secondary cooling area not only reduces the center segregation of the casting blank, but also enlarges the equiaxial crystals at the center of the slab, further improves the internal quality of the casting blank, and ensures various performances after the casting blank is rolled into a steel plate.
Drawings
The invention is further illustrated in the following description with reference to the drawings.
FIG. 1 shows the low-order effect of the cast slab according to the embodiment of the invention.
Detailed Description
In order to make the objects, technical solutions and advantages of the embodiments of the present invention clearer, the technical solutions in the embodiments of the present invention will be clearly and completely described below with reference to the embodiments.
Example (b):
the casting cross section was 2000X 250.
The condition of the sector section is checked before the casting, the sector section has no water leakage condition, and if a nozzle is blocked, the sector section needs to be replaced.
During casting, the Q1100D high-strength steel comprises the following chemical components in percentage by mass:
0.16% of C, 0.2% of Si, 1.15% of Mn, 0.008% of P, 0.002% of S, 0.027% of Alt, 0.025% of Als, 0.025% of Nb, 0.055% of V, 0.02% of Ti, 0.25% of Cr, 0.6% of Mo, 0.35% of Ni, 0.0017% of Ca, 0.0015% of B, and the balance of Fe and inevitable impurities.
The water flow of the crystallizer is 4300L/min, the water flow of the narrow side is 370L/min, the water temperature of the crystallizer can fluctuate slightly, but the temperature is controlled to be 35-38 ℃, so that the hot-flow density in the crystallizer is 1100-1200KW/m during casting2The heat flux density in this range ensures the casting safety and does not cause cracks.
Because the water temperature and the secondary cooling water temperature of the 1 st furnace crystallizer are both low, and the time is required for the pulling speed to rise from 0 to the normal pulling speed after casting, the vibration trace of the casting blank is deep, and the probability of cracks is high, the Q1100D needs to be arranged after the 2 nd furnace in the same casting time for casting, and the probability of cracks is obviously reduced.
The superheat degree of the molten steel is gradually reduced during casting, but the molten steel needs to be stabilized between 15 and 25 ℃, and the drawing speed is stabilized at 1.0 m/min.
The secondary cooling water temperature is stabilized at 28 ℃, the specific water quantity adopts 0.8L/kg steel, and the water quantity of each secondary cooling area is as follows:
TABLE 1 amount of secondary cooling water
The mold flux used was a Qingdao Scobiger model YK2P-3 mold flux having a viscosity of 0.77Pa.s and a melting point of 1141 ℃. During casting, the liquid slag layer is measured to be 12mm, and the slag consumption is measured to be 0.46 kg/ton steel.
The double-cold-zone electromagnetic stirring device adopts double-roller type electromagnetic stirring, is respectively arranged at the outlet of the sector 3 section and the inlet of the sector 4 section, and has the current of 330A and the frequency of 5 Hz. At the moment, a butterfly flow field is formed, the stirring effect is optimal, and the center segregation is lightest.
The soft reduction adopts sector 8, 9 and 10 sections of reduction, and the reduction is respectively 3.3mm, 3.3mm and 1.5 mm.
After the casting blank is cut, the casting blank is directly fed into a slow cooling pit in a downward line mode, hot charging is not needed, a burner is arranged in the slow cooling pit, the burner is ignited before the casting blank is fed downward, and the pit is filled with a rear cover. The slow cooling aims at eliminating the residual stress of the casting blank and is more beneficial to the quality of the inner part and the outer part of the casting blank. And after slowly cooling for 72 hours, the steel plate can be subjected to furnace rolling.
The casting blank prepared by casting through the technical measures has good surface quality, good center segregation condition and low-power rating of C0.5, and has no intermediate cracks or center cracks. After the casting blank is rolled into a steel plate, the surface has no defects, and various performance indexes meet the requirements, and the specific performance is as follows:
TABLE 2 mechanical Properties of the Steel sheets
The above description is only a preferred embodiment of the present invention, and it should be noted that various changes and modifications to the present invention without departing from the principle of the present invention should fall within the protection scope defined by the appended claims.
The above-described embodiments are merely illustrative of the preferred embodiments of the present invention, and do not limit the scope of the present invention, and various modifications and improvements of the technical solutions of the present invention can be made by those skilled in the art without departing from the spirit of the present invention, and the technical solutions of the present invention are within the scope of the present invention defined by the claims.
Claims (4)
1. A Q1100D ultrahigh-strength steel casting method is characterized by comprising the following steps:
(1) the Q1100D high-strength steel comprises the following chemical components in percentage by mass:
0.16 percent of C, 0.2 percent of Si, 1.15 percent of Mn, less than or equal to 0.008 percent of P, less than or equal to 0.002 percent of S, 0.027 percent of Alt, 0.025 percent of Als, 0.025 percent of Nb, 0.055 percent of V, 0.02 percent of Ti, 0.25 percent of Cr, 0.6 percent of Mo, 0.35 percent of Ni, 0.0017 percent of Ca, 0.0015 percent of B, and the balance of Fe and inevitable impurities;
(2) the casting section adopts a 2000 multiplied by 250 section;
(3) in order to ensure the surface quality of a casting blank, the technical measures adopted comprise:
A. the water quantity of the crystallizer is 4300L/min, the water quantity of the narrow side is 370L/min, and the water temperature of the crystallizer is 35-38 ℃;
B. the temperature of the secondary cooling water is stabilized at 28 ℃, and the specific water amount is 0.80L/kg steel;
C. the casting pulling speed is stabilized at 1.0 m/min;
D. medium-carbon high-manganese low-alloy type covering slag is used as the crystallizer covering slag, the viscosity is required to be 0.7-1.2Pa.s, and the melting point is 1100-1150 ℃;
E. before casting, checking the radian and the opening degree of the sector section, wherein the radian error is required to be less than or equal to 0.3 mm; the error of the opening degree is less than or equal to 1 mm;
(4) in order to ensure the internal quality of a casting blank, the technical measures adopted comprise:
A. controlling the superheat degree of molten steel at 15-25 ℃ during casting;
B. adopting secondary cooling electromagnetic stirring, and respectively installing a double-roller type mixer at the outlet of the sector 3 section and the inlet of the sector 4 section, wherein the current is 330A, and the frequency is 5 Hz;
C. the soft reduction adopts three sections of sector 8, 9 and 10 for reduction, the reduction amount is respectively 3.3mm,
3.3mm、1.5mm；
(5) And (3) after casting a casting blank, not carrying out hot charging, and taking the casting blank off the line to a slow cooling pit with a heating function in a slow cooling mode for more than 72 hours.
2. The method for casting the Q1100D ultrahigh-strength steel according to claim 1, wherein the other lower grade steel grade is arranged in the furnace 1 during casting, and the Q1100D steel grade according to the invention is arranged after the water temperature is stabilized after the furnace 2.
3. The method for casting the ultrahigh-strength steel Q1100D according to claim 1, wherein the mold flux is a type YK2P-3 mold flux of the sinoislando sbury type having a viscosity of 0.77pa.s and a melting point of 1141 ℃.
4. The method for casting the Q1100D ultrahigh-strength steel according to claim 3, wherein a liquid slag layer is measured for 12mm and a slag consumption is measured for 0.46 kg/ton steel.
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN115069998A (en) * | 2022-07-03 | 2022-09-20 | 新疆八一钢铁股份有限公司 | Heat-preservation hot charging method for steel rolling medium plate blank |
| CN115094297A (en) * | 2022-05-06 | 2022-09-23 | 包头钢铁（集团）有限责任公司 | Production method of thick Q420Q steel |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6125919A (en) * | 1997-08-26 | 2000-10-03 | Sumitomo Metal Industries, Ltd. | Mold powder for continuous casting and method of continuous casting |
| CN103451554A (en) * | 2013-09-03 | 2013-12-18 | 上海清河机械有限公司 | Metal material for valve box, and preparation method thereof |
| CN107838390A (en) * | 2017-10-27 | 2018-03-27 | 舞阳钢铁有限责任公司 | A kind of method for improving big cross section peritectic steel continuous casting billet quality |
| CN111254361A (en) * | 2020-03-31 | 2020-06-09 | 湖南华菱湘潭钢铁有限公司 | Production method of Q1100D/E extra-thin steel plate for high-strength structure |
| CN111876678A (en) * | 2020-07-14 | 2020-11-03 | 马鞍山钢铁股份有限公司 | Process method for solving cracks of high-strength steel casting blank |
| CN113664174A (en) * | 2021-07-02 | 2021-11-19 | 包头钢铁（集团）有限责任公司 | Production method of steel S355NL commodity blank for wind power flange |
-
2021
- 2021-12-16 CN CN202111546160.2A patent/CN114346194A/en active Pending
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6125919A (en) * | 1997-08-26 | 2000-10-03 | Sumitomo Metal Industries, Ltd. | Mold powder for continuous casting and method of continuous casting |
| CN103451554A (en) * | 2013-09-03 | 2013-12-18 | 上海清河机械有限公司 | Metal material for valve box, and preparation method thereof |
| CN107838390A (en) * | 2017-10-27 | 2018-03-27 | 舞阳钢铁有限责任公司 | A kind of method for improving big cross section peritectic steel continuous casting billet quality |
| CN111254361A (en) * | 2020-03-31 | 2020-06-09 | 湖南华菱湘潭钢铁有限公司 | Production method of Q1100D/E extra-thin steel plate for high-strength structure |
| CN111876678A (en) * | 2020-07-14 | 2020-11-03 | 马鞍山钢铁股份有限公司 | Process method for solving cracks of high-strength steel casting blank |
| CN113664174A (en) * | 2021-07-02 | 2021-11-19 | 包头钢铁（集团）有限责任公司 | Production method of steel S355NL commodity blank for wind power flange |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN115094297A (en) * | 2022-05-06 | 2022-09-23 | 包头钢铁（集团）有限责任公司 | Production method of thick Q420Q steel |
| CN115069998A (en) * | 2022-07-03 | 2022-09-20 | 新疆八一钢铁股份有限公司 | Heat-preservation hot charging method for steel rolling medium plate blank |
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Application publication date: 20220415 |