CN115369306A - Method for improving non-metallic inclusions in 1Ni3MnCuMoAl large steel ingots - Google Patents
Method for improving non-metallic inclusions in 1Ni3MnCuMoAl large steel ingots Download PDFInfo
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Abstract
The invention provides a method for improving nonmetallic inclusions in a 1Ni3MnCuMoAl large steel ingot, which comprises the following steps: (1) smelting: adopting an IM furnace, an LF furnace and a VD furnace, and controlling the casting temperature at 1540-1550 ℃; adding Ti with the mass fraction of 0.02-0.04% in the smelting process; (2) electroslag: adopting common electroslag or protective atmosphere electroslag smelting; (3) forging: the initial forging temperature is controlled to be 1180-1250 ℃, the final forging temperature is controlled to be 850-900 ℃, and the forging heating adopts 550 ℃ plus 850 ℃ for preheating. According to the difference of the precipitation temperature of AlN and TiN, the precipitation temperature of TiN is higher than that of AlN, a small amount of Ti is added into the original components of the smelted die steel, the content of Ti is controlled to be 0.02-0.04%, tiN is promoted to be formed, tiN is preferentially precipitated, the number and the size of the precipitated TiN inclusions are greatly reduced compared with the original AlN inclusions, the content of the nonmetallic inclusions larger than 5 mu m is reduced to 20% from 90%, and the polishing performance is improved to 10000# from the original 8000 #.
Description
Technical Field
The invention belongs to the technical field of alloy materials, and particularly relates to a method for improving nonmetallic inclusions in a 1Ni3MnCuMoAl large steel ingot.
Background
In recent years, the mold steel industry in China is rapidly developed, and particularly the development of the plastic industry promotes the overall development of the plastic mold steel industry level. The rapid development of the plastic mold industry also puts higher requirements on the purity, polishing performance, fine grain structure and the like of the mold steel.
The high-mirror surface die steel is a material with higher requirements in plastic dies, is widely applied to the industries of automobiles, mobile phones, household appliances and high-end electronic products, and the die material needs to bear the influence of external factors such as high pressure, corrosion, abrasion and the like, so that the requirement on the comprehensive mechanical property of the material is higher, the property uniformity of the material is required, and the hardness of the material is also ensured. In addition, the content of non-metallic inclusions in the material affects the purity of the die steel and also affects the polishing performance of the die steel.
The 1Ni3MnCuMoAl is corresponding to Japanese trade mark NAK80, is pre-hardened plastic mold steel, is delivered in a pre-hardened state, does not need reheating treatment, and is widely applied in the plastic direction due to good polishing property and carving decoration property. The purity of the steel directly determines the polishing performance of the steel, and the number and the size of inclusions tend to increase and grow with the increase of ingot shapes (6T → 8T → 12T) in actual production. However, the polishing performance is poor and can only be used for some mold products with low polishing requirements. The inclusions of the steel are mainly AlN through electron microscope analysis, the AlN inclusions with the size larger than 5mm account for nearly 90 percent, the polishing performance of the steel is seriously influenced (the polishing performance of the steel is mainly related to the number and the size of the inclusions), and particularly, the number and the size of AlN precipitates are increased along with the increase of an ingot.
Patent document CN 110565014A discloses a production process of a high-mirror plastic die steel 1Ni3MnCuMoAl thick plate, the patent method selects high-quality scrap steel for steel making in an electric furnace, uses steel ingots for secondary firing to form materials, and obtains the high-mirror plastic die steel 1Ni3MnCuMoAl thick plate with excellent internal quality and good processing performance through a reasonable heating mode, a rolling process and an age hardening heat treatment system, the maximum thickness of the steel plate reaches 110mm, and the flaw detection meets the requirements of GB/T2970 level I. The high-mirror-surface plastic die steel 1Ni3MnCuMoAl thick plate has good comprehensive performance, the surface quality of the steel plate is improved compared with that of a forged material, the steel plate has uniform structure, excellent processing and polishing performance, low inclusion level and greatly reduced production cost compared with a product made of a forged material. The inclusions are detected according to the GB/T10561A method, the total grade of the inclusions of the die steel is not more than 2.5, the steel plate structure is granular bainite and a small amount of residual austenite, and the hardness of the steel plate is 38-43HRC. However, the inclusion level is still to be further improved and the polishing performance is still to be improved.
Since the demand for the 1Ni3MnCuMoAl ingot type of the plastic mold steel is continuously increasing, a large amount of 1Ni3MnCuMoAl mold steel having a large ingot type needs to be prepared. However, the larger the ingot type is, the more the number of inclusions is, the larger the size of the steel is, and the polishing performance of the steel is seriously affected. Therefore, how to reduce the content of large-size inclusions in large-size 1Ni3MnCuMoAl ingots and improve the polishing performance of the ingots needs to be further developed.
Disclosure of Invention
The invention aims to solve the problems, and provides a method for improving the content of large-size impurities in a large-size 1Ni3MnCuMoAl steel ingot so as to solve the problems of high content of non-metal impurities and poor polishing performance in the existing preparation process of the large-size 1Ni3MnCuMoAl steel ingot.
In order to solve the technical problems, the technical scheme adopted by the invention is as follows:
a method for improving non-metallic inclusions in large 1Ni3MnCuMoAl steel ingots comprises the following steps:
(1) Smelting: adopting an IM furnace, an LF furnace and a VD furnace, and controlling the casting temperature at 1540-1550 ℃; adding Ti with the mass fraction of 0.02-0.04% in the smelting process;
(2) Electroslag: adopting common electroslag or electroslag smelting in protective atmosphere;
(3) Forging: the initial forging temperature is controlled to be 1180-1250 ℃, the final forging temperature is controlled to be 850-900 ℃, and the forging heating adopts 550 ℃ plus 850 ℃ for preheating.
The invention adopts IM (intermediate frequency furnace) + LF + VD (external refining), and simultaneously, the precipitation temperature of TiN is higher than AlN according to the different precipitation temperatures of AlN and TiN, the invention adds a trace amount of Ti into the original components of the smelted die steel, controls the content of Ti to be 0.02-0.04%, finds that TiN can be promoted to be formed, so that AlN is preferentially precipitated, the quantity and the size of the precipitated TiN inclusions are greatly reduced compared with the original AlN inclusions, the content of the nonmetallic inclusions larger than 5 mu m after the trace amount of Ti is treated is reduced to be less than 20% from more than 90%, and simultaneously the polishing performance of the nonmetallic inclusions is obviously improved, and the polishing performance is improved to 10000# from the original 8000 #.
Because the large 1Ni3MnCuMoAl steel ingot contains high Al, the solidification speed is gradually reduced along with the increase of the ingot shape in production, and a large amount of AlN inclusions are precipitated. The process provided by the invention is based on the optimization of the percentage of chemical components, the micro Ti inclusion modification treatment is carried out through the following thermodynamic calculation formulas (1) and (2), the nitrogen control is enhanced to enable the nitrogen to be less than or equal to 20ppm, the size and the number of the inclusions in the large ingot type (12T) of the material are greatly reduced, and the polishing performance of the material after solution aging is improved from the original 8000# to 10000#.
(1) Thermodynamic formula for AlN precipitation (unit: K)
Solid solubility product formula:
(2) Thermodynamic formula of TiN precipitation (unit: K)
Solid solubility product formula:
calculated by the above formula: when the mass percentage content of Ti is controlled to be 0.02-0.04%, the titanium nitride is precipitated in preference to aluminum nitride, the precipitation quantity and size are greatly reduced, the quality level of inclusions in the steel large ingot is powerfully improved, and the polishing performance of the steel large ingot is improved.
Further, the 1Ni3MnCuMoAl large steel ingot comprises the following elements in percentage by weight: c:0.08 to 0.20, mn:1.40 to 2.00%, si: less than or equal to 0.45 percent, mn: less than or equal to 0.8 percent, S: less than or equal to 0.15 percent, P: less than or equal to 0.03%, ni:2.90 to 3.40%, cu:0.80 to 1.20%, mo:0.20 to 0.50%, al:0.70 to 1.20%, ti:0.02 to 0.04%, N: less than or equal to 20ppm, and the balance being Fe.
Further, the scale of the 1Ni3MnCuMoAl large-sized steel ingot is 12T.
Further, after the forging of the step (3) is completed, solution treatment and aging treatment are also included.
Further, the temperature of the solution treatment is 860-880 ℃, the time of the solution treatment is 1.8-2.4min/mm, and the product is discharged from a furnace and cooled in air.
Further, the temperature of the aging treatment is 520-550 ℃, the time of the aging treatment is 1.6-2.0min/mm, and the steel plate is discharged from a furnace and cooled in air.
Compared with the prior art, the invention has the following beneficial effects:
(1) The invention provides a method for improving nonmetallic inclusions in 1Ni3MnCuMoAl large steel ingots, which is characterized in that the modification treatment of micro Ti inclusions is carried out by a thermodynamic calculation formula from the percentage of optimized chemical components, the nitrogen control is enhanced, the nitrogen is less than or equal to 20ppm, the size and the number of the inclusions in a large ingot of the material are greatly reduced, and the polishing performance of the material is improved from the original 8000# to 10000# after solution treatment and aging.
(2) The method can obtain the large-size 1Ni3MnCuMoAl steel ingot, can prepare the large-size 1Ni3MnCuMoAl steel ingot with the scale of 12T, and can well control the content of non-metallic inclusions and improve the polishing performance of the steel ingot.
Detailed Description
The technical solutions in the embodiments of the present invention will be clearly and completely described below with reference to the embodiments of the present invention, and it is obvious that the described embodiments are only a part of the embodiments of the present invention, and not all of the embodiments. All other embodiments, which can be obtained by a person skilled in the art without making any creative effort based on the embodiments in the present invention, belong to the protection scope of the present invention.
Example 1 (conventional Process)
A1 Ni3MnCuMoAl large-sized steel ingot comprises the following original components with the control range as shown in the following table 1:
TABLE 1 compositional requirements (balance Fe not shown)
The non-metallic inclusion requirements of the steel are shown in table 2:
TABLE 2 non-metallic inclusion requirement of the steel
The steel is delivered in an aging state, and the requirement of delivering hardness HRC =38-42 is met.
The preparation process of the steel comprises the following steps:
(1) Smelting: adopting a steel furnace, and controlling the casting temperature to be 1540-1550 ℃;
(2) Electroslag: adopting common electroslag or electroslag smelting in protective atmosphere;
(3) Forging: controlling the initial forging temperature to 1180-1250 ℃, controlling the final forging temperature to 850-900 ℃, and preheating forging at 550 ℃ and 850 ℃;
(4) Solution treatment: the temperature is 860 to 880 ℃, the solution treatment time is 1.8 to 2.4min/mm, and the product is discharged from the furnace and cooled by air;
(5) Aging treatment: the temperature is 520-550 ℃, the aging treatment time is 1.6-2.0min/mm, and the product is discharged from the furnace and cooled in air.
In the practical production, the following components in percentage by weight are taken as examples of the 1Ni3MnCuMoAl steel ingot, wherein C:0.20%, mn:2.00%, si:0.45%, mn:0.8%, S:0.15%, P:0.03%, ni:3.40%, cu:1.20%, mo:0.50%, al:1.20 percent and the balance of Fe; controlling the casting temperature to be 1540 ℃, adopting common electroslag as electroslag, controlling the initial forging temperature to be 1180 ℃, the final forging temperature to be 850 ℃, and preheating the forging at 550 ℃ and 850 ℃; the solution treatment temperature is 860 ℃, the solution treatment time is 1.8min/mm, and the steel is discharged from a furnace and cooled by air; the aging treatment temperature is 520 ℃, the aging treatment time is 1.6min/mm, and the steel plate is discharged from a furnace and cooled in air.
As the Al content of the steel is higher, the solidification speed is gradually reduced along with the increase of the ingot type in production, and a large amount of AlN inclusions are precipitated, and the number and the size of the inclusions tend to increase and grow along with the increase of the ingot type (6T → 8T → 12T) in production. The polishing performance is poor, and the polishing agent can only be used for some mould products with low polishing requirements. The main component of the inclusion was AlN by electron microscope analysis (see Table 3).
TABLE 3 inclusion before 1Ni3MnCuMoAl (12T) ingot process adjustment
As can be seen from table 3, the inclusion distribution of the steel is mainly based on AlN and on inclusions (including other inclusions) having a size of more than 5 μm, which seriously affect the polishing properties of the steel (the polishing properties of the steel are mainly related to the number and size of inclusions). Particularly, the quantity and the size of AlN are increased along with the increase of the ingot type, so that the prior process can only produce 6T steel ingots and is not suitable for producing 12T large-sized steel ingots, because the larger the ingot type is, the quantity and the size of inclusions are increased and increased, and the polishing performance is seriously influenced.
Example 2 (modified Process)
In order to solve the problems existing in the conventional process, the following process improvements are made in the embodiment:
a method for improving non-metallic inclusions in large 1Ni3MnCuMoAl steel ingots comprises the following steps:
(1) Smelting: adopting an IM furnace, an LF furnace and a VD furnace, and controlling the casting temperature at 1540-1550 ℃; adding Ti with the mass fraction of 0.02-0.04% in the smelting process;
(2) Electroslag: adopting common electroslag or protective atmosphere electroslag smelting;
(3) Forging: controlling the initial forging temperature to 1180-1250 ℃, controlling the final forging temperature to 850-900 ℃, and preheating the forging at 550 ℃ and 850 ℃;
(4) Solution treatment: the temperature is 860 to 880 ℃, the solution treatment time is 1.8 to 2.4min/mm, and the product is discharged from the furnace and cooled by air;
(5) Aging treatment: the temperature is 520-550 ℃, the aging treatment time is 1.6-2.0min/mm, and the steel plate is discharged from a furnace and cooled in air.
According to the improved process, IM (intermediate frequency furnace) + LF + VD (external refining) is adopted in the smelting of the embodiment 1, the precipitation temperature of TiN is higher than that of AlN according to the different precipitation temperatures of AlN and TiN, trace Ti (0.02 wt% for example, and the balance being Fe is supplemented) is added into the raw components (C: 0.20%, mn:2.00%, si:0.45%, mn:0.8%, S:0.15%, P:0.03%, ni:3.40%, cu:1.20%, mo:0.50%, al: 1.20%) of the 1Ni3MnCuMoAl ingot to promote the formation of TiN, so that AlN inclusion is preferentially precipitated, the number and the size of the precipitated TiN are greatly reduced compared with those of the original AlN inclusion, the polishing performance is improved from the original 8000#, and the total inclusions are improved as shown in the following table 4:
TABLE 4 inclusions in steel ingots after micro Ti treatment of 1Ni3MnCuMoAl (12T)
As can be seen from the comparison between the inclusions before and after the adjustment in tables 3 and 4, the inclusion content of the inclusions larger than 5 μm after the micro Ti treatment is reduced to 19.5%, and the size of the inclusions is significantly reduced.
The improved process mainly optimizes the percentage of chemical components, performs modification treatment on micro Ti inclusions by the thermodynamic formula in the following table 5, strengthens nitrogen control to ensure that the nitrogen is less than or equal to 20ppm, greatly reduces the size and the number of the inclusions of the large ingot type (12T) of the material (see the comparison between the processes in the table 1 and the table 2), and improves the polishing performance to 10000# from the original 8000# after solution and aging.
TABLE 5 thermodynamic calculation formula
By calculation, when Ti is controlled to be 0.02-0.04wt%, the precipitation of titanium nitride in preference to aluminum nitride is greatly reduced in precipitation amount and size, the quality level of inclusions in the steel large ingot is improved powerfully, and the polishing performance of the steel large ingot is improved.
The modified process of the present invention has the following adjusted chemical components as shown in table 6 below:
TABLE 6 chemical composition contents after adjustment of the inventive process (balance Fe not shown)
Test example 1
Through the improved process of the embodiment 1, the inclusion content, the non-metallic inclusion grade and the polishing performance of the 1Ni3MnCuMoAl large steel ingot (12T) before and after the process adjustment are tested, and the results are shown in the following tables 7 to 9:
TABLE 7 comparison of inclusions before and after Process adjustment
TABLE 8 comparison of the stages before and after adjustment of the process for producing non-metallic inclusions in steel ingots (12T) of 1Ni3MnCuMoAl
TABLE 9 comparison of polishing Performance before and after Process adjustment for Large ingot of Ni3MnCuMoAl (12T)
Comparative example 1
The modified process of example 2 was followed, except that the content of Ti was controlled to 0.1wt%, and as a result, it was found that the presence of excess Ti affected the preferential precipitation of titanium nitride and promoted the simultaneous precipitation of a part of aluminum nitride. The distribution and content of total inclusions after excess Ti treatment are shown in table 10:
TABLE 10 inclusions in steel ingots after excess Ti treatment of 1Ni3MnCuMoAl (12T)
It will be evident to those skilled in the art that the invention is not limited to the details of the foregoing illustrative embodiments, and that the present invention may be embodied in other specific forms without departing from the spirit or essential attributes thereof. The present embodiments are therefore to be considered in all respects as illustrative and not restrictive, the scope of the invention being indicated by the appended claims rather than by the foregoing description, and all changes which come within the meaning and range of equivalency of the claims are therefore intended to be embraced therein. Any reference sign in a claim should not be construed as limiting the claim concerned.
Furthermore, it should be understood that although the present description refers to embodiments, not every embodiment may contain only a single embodiment, and such description is for clarity only, and those skilled in the art should integrate the description, and the embodiments may be combined as appropriate to form other embodiments understood by those skilled in the art.
Claims (6)
1. A method for improving non-metallic inclusions in large 1Ni3MnCuMoAl steel ingots is characterized by comprising the following steps:
(1) Smelting: adopting an IM furnace, an LF furnace and a VD furnace, and controlling the casting temperature at 1540-1550 ℃; adding 0.02-0.04wt% of Ti in the smelting process;
(2) Electroslag: adopting common electroslag or protective atmosphere electroslag smelting;
(3) Forging: the initial forging temperature is controlled to be 1180-1250 ℃, the final forging temperature is controlled to be 850-900 ℃, and the forging heating adopts 550 ℃ plus 850 ℃ for preheating.
2. The method according to claim 1, wherein the 1Ni3MnCuMoAl large ingot has an elemental composition, in weight percent: c:0.08 to 0.20, mn:1.40 to 2.00%, si: less than or equal to 0.45 percent, mn: less than or equal to 0.8 percent, S: less than or equal to 0.15 percent, P: less than or equal to 0.03 percent, ni:2.90 to 3.40%, cu:0.80 to 1.20%, mo:0.20 to 0.50%, al:0.70 to 1.20%, ti:0.02 to 0.04%, N: less than or equal to 20ppm, and the balance being Fe.
3. A method according to claim 1 or 2, characterized in that the scale of the 1Ni3MnCuMoAl large ingot is 12T.
4. The method according to claim 1 or 2, further comprising solution treatment and aging treatment after the forging of step (3) is completed.
5. The method according to claim 4, wherein the solution treatment temperature is 860 to 880 ℃, the solution treatment time is 1.8 to 2.4min/mm, and the product is discharged from the furnace and cooled by air.
6. The method of claim 4, wherein the aging treatment temperature is 520-550 ℃, the aging treatment time is 1.6-2.0min/mm, and the product is discharged from the furnace and cooled in air.
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| CN113106339A (en) * | 2021-03-22 | 2021-07-13 | 北京科技大学 | Preparation method of ultrahigh-strength high-plasticity high-temperature-oxidation-resistant hot stamping formed steel |
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