A production process control method for high-aluminum and high-titanium iron-nickel based alloy

Abstract

The present invention relates to the technical field of alloy smelting, and specifically to a production process control method for a high-aluminum and high-titanium iron-nickel-based alloy, comprising: obtaining a stirring feature F1 when the aluminum and titanium content in the slag is the smallest and a stirring feature F2 when the stirring time is the smallest, obtaining a first stirring feature when the slag is optimal and a second stirring feature when the stirring time is the smallest according to the aluminum and titanium content in the slag; obtaining a final stirring feature according to the difference in slag composition corresponding to the first stirring feature of F1 and F1, the sum of the stirring time of the second stirring feature of F1 and F1, and the difference in slag composition corresponding to the second stirring feature of F2 and F2, and the sum of the stirring time of the first stirring feature of F2 and F2, the final stirring feature is the stirring feature when argon is blown at the bottom after adding aluminum and titanium elements. The present invention further prevents slag rolling and secondary oxidation, and improves production efficiency.

Description

Technical Field

[0001] The invention relates to the technical field of alloy smelting, and in particular to a production process control method for a high-aluminum and high-titanium iron-nickel based alloy. Background Art

[0002] When smelting high-aluminum and high-titanium iron-nickel-based alloys, the traditional smelting methods include LF refining outside the furnace and electroslag remelting, among which electroslag remelting has a high production cost, and the Al and Ti elements may be burned during the electroslag remelting process, resulting in unstable product performance; during the LF refining outside the furnace, it is necessary to adjust the aluminum and titanium content in the molten steel by adding aluminum wire and pure titanium, and stir by blowing argon gas at the bottom to promote the floating and removal of debris such as slag, but the unreasonable control of the strength of the blown argon gas will lead to secondary oxidation problems or the slag debris will be drawn into the molten steel to adsorb aluminum and titanium elements, making the aluminum and titanium content in the molten steel not meet the requirements. Therefore, the existing smelting method cannot further efficiently smelt qualified high-aluminum and high-titanium iron-nickel-based alloys, especially when the electroslag remelting process is saved, due to the unreasonable control of the strength of the argon gas blown during the LF refining outside the furnace, the qualified rate and production efficiency of the high-aluminum and high-titanium iron-nickel-based alloy will be significantly reduced. Summary of the invention

[0003] In order to solve the above problems, the present invention provides a production process control method for a high-aluminum and high-titanium iron-nickel based alloy.

[0004] The production process control method of a high-aluminum and high-titanium iron-nickel based alloy of the present invention adopts the following technical scheme:

[0005] The present invention discloses a production process control method for a high-aluminum and high-titanium iron-nickel-based alloy. The production process in the method comprises EAF roughing, AOD refining, LF refining and die casting; during the LF refining, aluminum and titanium elements are added to the molten steel, and when argon is blown at the bottom for stirring, after argon is blown for a time length of T1, the blowing amount of argon decreases linearly, and the time length of the linear decrease is T2; T1 and T2 are recorded as stirring characteristics, and the sum of T1 and T2 is recorded as the stirring time of the stirring characteristic, and at the end of stirring, the slag is sampled and tested to obtain the slag composition corresponding to the stirring characteristic;

[0006] After adding aluminum and titanium elements, the stirring characteristics F1 when the slag is optimal and the stirring characteristics F2 when the stirring time is minimum are obtained according to the amount of aluminum and titanium elements added; the optimal slag refers to the time when the aluminum and titanium content in the slag is the minimum;

[0007] For any stirring feature F in F1 and F2, the slag composition corresponding to the stirring feature F is recorded as Q;

[0008] According to the amount of aluminum and titanium elements in the slag component Q, the stirring characteristic when the slag is optimal and the stirring characteristic when the stirring time is minimum are obtained, and they are recorded as the first stirring characteristic and the second stirring characteristic of the stirring characteristic F respectively;

[0009] The difference between the slag composition corresponding to the stirring feature F1 and the slag composition corresponding to the first stirring feature of the stirring feature F1, and the sum of the stirring time of the stirring feature F1 and the stirring time of the second stirring feature of the stirring feature F1 are recorded as the supplementary stirring feature of the stirring feature F1;

[0010] The difference between the slag composition corresponding to the stirring feature F2 and the slag composition corresponding to the second stirring feature of the stirring feature F2, and the sum of the stirring time of the stirring feature F2 and the stirring time of the first stirring feature of the stirring feature F2 are recorded as the additional stirring feature of the stirring feature F2;

[0011] The final stirring characteristic is obtained according to the supplementary stirring characteristic of the stirring characteristic F1 and the supplementary stirring characteristic of the stirring characteristic F2, and the final stirring characteristic is the stirring characteristic when argon is blown at the bottom after adding the aluminum and titanium elements.

[0012] Preferably, the specific steps for obtaining the additional stirring feature of the stirring feature F1 and the additional stirring feature of the stirring feature F2 are as follows:

[0013] The amount of aluminum and titanium in the slag composition corresponding to the stirring feature F1 is recorded as fa1, and the amount of aluminum and titanium in the slag composition corresponding to the first stirring feature of the stirring feature F1 is recorded as fb1; the sum of the stirring time of the stirring feature F1 and the stirring time of the second stirring feature of the stirring feature F1 is recorded as t1, and the additional stirring feature of the stirring feature F1 includes: slag difference fa1-fb1, time consumption t1;

[0014] The amount of aluminum and titanium elements in the slag composition corresponding to the stirring feature F2 is recorded as fa2, and the amount of aluminum and titanium elements in the slag composition corresponding to the second stirring feature of the stirring feature F2 is recorded as fb2; the sum of the stirring time of the stirring feature F2 and the stirring time of the first stirring feature of the stirring feature F2 is recorded as t2, and the supplementary stirring characteristics of the stirring feature F2 include: slag difference fa2-fb2, and time consumption t2.

[0015] Preferably, the final stirring feature is obtained according to the additional stirring feature of the stirring feature F1 and the additional stirring feature of the stirring feature F2, and the specific steps include the following:

[0016] Obtaining a reference coefficient of the stirring feature F1, wherein the reference coefficient of the stirring feature F1 is positively correlated with the slag difference of the stirring feature F1, and the reference coefficient of the stirring feature F1 is negatively correlated with the time consumption of the stirring feature F1;

[0017] Obtaining a reference coefficient of the stirring feature F2, wherein the reference coefficient of the stirring feature F2 is positively correlated with the slag difference of the stirring feature F2, and the reference coefficient of the stirring feature F2 is negatively correlated with the time consumption of the stirring feature F2;

[0018] Final mixing characteristics ,in , They respectively represent the reference coefficient of the stirring feature F1 and the reference coefficient of the stirring feature F2.

[0019] Preferably, the specific steps for obtaining the reference coefficient of the stirring feature F1 and the reference coefficient of the stirring feature F2 are as follows:

[0020] Aluminum and titanium elements have been added several times during the LF refining process, the number of times the aluminum and titanium elements have been added is recorded as n, and the duration of LF refining is recorded as tt; for any stirring feature F in F1 and F2, the ratio of the slag difference of the stirring feature F to n is recorded as the first ratio, the product of the time consumption of the stirring feature F and tt is recorded as the first product, and the reference coefficient of the stirring feature F is equal to the ratio of the first ratio to the first product.

[0021] Preferably, the step of obtaining the stirring characteristic F1 when the slag is optimal and the stirring characteristic F2 when the stirring time is minimum according to the amount of added aluminum and titanium elements comprises the following specific steps:

[0022] During each LF refining process in history, the weight of aluminum and titanium elements added each time, the stirring feature used, the stirring time of the stirring feature, and the slag composition corresponding to the stirring feature are recorded as a historical record;

[0023] For the ongoing LF refining process, the weight of the added aluminum and titanium elements is obtained and recorded as the first weight. In the historical records, several historical records with the smallest difference from the first weight are obtained and recorded as reference records.

[0024] A reference record with the smallest aluminum and titanium content in the slag composition is obtained from the reference records, and the stirring characteristics contained in the reference record with the smallest aluminum and titanium content are used as the stirring feature F1; a reference record with the smallest stirring time is obtained from the reference records, and the stirring characteristics contained in the reference record with the smallest stirring time are used as the stirring feature F2.

[0025] Preferably, the chemical composition of the high-aluminum and high-titanium iron-nickel based alloy is as follows by mass percentage: C≤0.08%, Si≤1%, Mn≤3%, P≤0.03%, S≤0.02%, Cr: 13.5%~16%, Ni: 24%~27%, Mo: 1%~1.5%, Al≤0.35%, Ti: 1.9%~2.35%, and B: 0.001%~0.01%.

[0026] Preferably, in the EAF rough refining stage, the tapping temperature is controlled between 1550 and 1650° C., and the Si content of the tapping steel is controlled between 0.1% and 0.4%.

[0027] Preferably, in the AOD refining stage, lime is added during the oxidation period, and the temperature is controlled at 1680-1720°C at the end of oxygen decarburization; during the pre-reduction period, ferrosilicon reduction process is adopted, ferrosilicon and slag-removing agent are added, and the slag basicity is controlled to be greater than 1.5, and the slag is scraped cleanly after completion; during the reduction period, lime and slag-removing agent are added, and aluminum ingots and pure titanium are supplemented;

[0028] The slag composition is controlled to 50~60%CaO+20~25%SiO2+10~20%Al2O3+6~12%TiO2+2~5%MgO+5~12%CaF2.

[0029] Preferably, in the LF refining stage, T2 is not less than 20 minutes, and the stirring time of the stirring characteristic is not less than 80 minutes; the tapping temperature of the molten steel is controlled to be 1500~1560℃.

[0030] Preferably, during the die casting stage, the mold temperature is controlled between 40 and 90°C; the protective slag is protected by the bottom laying method, and a high-efficiency heating agent is added to the riser before the end of casting, and the heating agent is evenly dispersed; argon gas protection is used for die casting, and argon gas protection is used during the pouring process.

[0031] The beneficial effects of the technical solution of the present invention are:

[0032] The present invention adopts a production process without electroslag remelting, which ensures the quality of the alloy and reduces the production cost.

[0033] After adding aluminum and titanium elements, the present invention obtains the stirring feature F1 when the slag is optimal and the stirring feature F2 when the stirring time is the smallest according to the amount of aluminum and titanium elements added; the stirring feature F1 describes: when performing bottom blowing argon stirring, the stirring feature required to minimize the amount of aluminum and titanium elements in the slag; this stirring feature can avoid slag roll-up and secondary oxidation problems as much as possible, so that after adding aluminum wire and pure titanium once or a few times, the aluminum and titanium content in the molten steel can meet the target component requirements. The stirring feature F2 when the stirring time is the smallest represents: the stirring feature used when the stirring time consumed is the smallest or the LF processing efficiency is maximized.

[0034] Furthermore, the present invention obtains a supplementary stirring feature of stirring feature F1 and a supplementary stirring feature of stirring feature F2. The supplementary stirring feature of stirring feature F1 and the supplementary stirring feature of stirring feature F2 describe: in order to prevent slag rolling and secondary oxidation problems and shorten the stirring time (that is, shorten the LF processing time), when stirring, the stirring conditions that exist when aluminum wire and pure titanium are added for the previous time and when aluminum wire and pure titanium are added for the next time, including the slag difference and time consumption caused by stirring.

[0035] Further, the final stirring feature is obtained according to the additional stirring feature of the stirring feature F1 and the additional stirring feature of the stirring feature F2. The present invention combines the stirring conditions required for the previous addition of aluminum wire and pure titanium and the next addition of aluminum wire and pure titanium to obtain a new stirring feature (i.e., the final stirring feature), avoiding the problem of multiple additions of aluminum wire and pure titanium and excessive time consumption caused by slag rolling and secondary oxidation problems, or avoiding the problem of deviation of the components in the molten steel from the target content and low refining efficiency caused by slag rolling and secondary oxidation problems, thereby ensuring the production efficiency of high-aluminum and high-titanium iron-nickel-based alloys and the qualified rate of products. BRIEF DESCRIPTION OF THE DRAWINGS

[0036] In order to more clearly illustrate the embodiments of the present invention or the technical solutions in the prior art, the drawings required for use in the embodiments or the description of the prior art will be briefly introduced below. Obviously, the drawings described below are only some embodiments of the present invention. For ordinary technicians in this field, other drawings can be obtained based on these drawings without paying creative work.

[0037] Figure 1 A flow chart of the steps of a production process control method for a high-aluminum and high-titanium iron-nickel based alloy provided by one embodiment of the present invention. DETAILED DESCRIPTION

[0038] In order to further explain the technical means and effects adopted by the present invention to achieve the predetermined invention purpose, the following is a detailed description of the production process control method of a high-aluminum and high-titanium iron-nickel-based alloy proposed by the present invention, its specific implementation method, structure, characteristics and effects, in combination with the accompanying drawings and preferred embodiments. In the following description, different "one embodiment" or "another embodiment" does not necessarily refer to the same embodiment. In addition, specific features, structures or characteristics in one or more embodiments may be combined in any suitable form.

[0039] Unless defined otherwise, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which this invention belongs.

[0040] The following is a specific scheme of a production process control method for a high-aluminum and high-titanium iron-nickel based alloy provided by the present invention.

[0041] It should be noted that the chemical composition of the high aluminum and high titanium iron-nickel-based alloy of the present invention includes: C≤0.08%, Si≤1%, Mn≤3%, P≤0.03%, S≤0.02%, Cr 13.5%~16%, Ni 24%~27%, Mo 1%~1.5%, Al≤0.35%, Ti1.9%~2.35%, B 0.001%~0.01%, and the remaining element is Fe. The above contents are expressed in mass percentage.

[0042] Embodiment 1:

[0043] This embodiment provides a production method of a high-aluminum and high-titanium iron-nickel based alloy, the production method comprising:

[0044] Step S101: EAF rough refining.

[0045] The charge is added to the EAF furnace (electric arc furnace) in three batches, the tapping temperature is between 1550 and 1650°C, and the Si content of the tapping is about 0.10% to 0.40%. The tapping temperature of this embodiment is controlled at 1550°C, and the Si content of the tapping is 0.40%. In other embodiments, the Si content of the tapping can be set to 0.30% or 0.10%, which helps to improve the hot working performance. In other embodiments, the tapping temperature can also be set to 1600°C or 1650°C.

[0046] S102, AOD refining.

[0047] The AOD refining process includes an oxidation period, a pre-reduction period and a reduction period in sequence.

[0048] Lime is added during the oxidation period, and other alloys such as high carbon ferrochromium, ferromolybdenum, water-quenched nickel, etc. are added according to the requirements of the molten steel composition.

[0049] In this embodiment, the target composition and target content of the molten steel are: 0.08% C, 1% Si, 3% Mn, 0.03% P, 0.02% S, 13.5% Cr, 24% Ni, 1% Mo, 0.35% Al, 1.9% Ti, 0.001% B, and the remaining elements are Fe. In other embodiments, the composition of the molten steel can be set to other values. For example, in other embodiments, in order to further improve the corrosion resistance of the alloy, the C content can be reduced, for example, the C content is reduced to 0.05% or less, and the Cr, Ni, and Mo contents are increased, for example, to 14.5%, 25%, and 1.3%, respectively, and at most to 16%, 27%, and 1.5%, respectively. In other embodiments, in order to improve the toughness of the alloy, the contents of C, P, and S can be further reduced, for example, the contents of P and S are reduced to 0.02% and 0.01%, and the Ti content is increased to a maximum of 2.35%. For another example, the content of B is increased to a maximum of 0.01%, so as to improve the grain boundary strength and creep resistance.

[0050] The temperature at the end of oxygen decarburization is about 1680-1720°C. In this embodiment, the temperature of oxygen decarburization is raised to 1680°C, and in other embodiments, the temperature can be raised to 1700°C or 1720°C; in the pre-reduction period, a ferrosilicon reduction process is adopted, ferrosilicon and slag-removing agent are added, and the slag basicity is controlled to be greater than 1.5. In this embodiment, the basicity is controlled at 1.6, and the slag is scraped off after the end; in the reduction period, lime and slag-removing agent are added, and aluminum ingots, pure titanium, pure nickel and other alloys are added according to the requirements of the molten steel composition.

[0051] The slag composition is controlled to 50~60%CaO+20~25%SiO2+10~20%Al2O3+6~12%TiO2+2~5%MgO+5~12%CaF2.

[0052] S103, LF refining outside the furnace.

[0053] By adding aluminum wire and pure titanium, the content of Al and Ti elements in the molten steel is controlled to meet the target composition requirements;

[0054] Stirring is performed by blowing argon from the bottom. The bottom blowing adopts a mode of strong blowing first and then gradually weakening. The weak stirring time is not less than 20 minutes to promote the removal of inclusions while preventing slag rolling and secondary oxidation. The LF treatment time is not less than 80 minutes. In this embodiment, the weak stirring time is set to 20 minutes, and the LF treatment time is set to 80 minutes. In other embodiments, the weak stirring time can be set to 40 minutes, and the LF treatment time can be set to 120 minutes. In this embodiment, 0.8 cubic meters of argon are blown out per minute during the strong blowing stage, and the argon is gradually weakened to 0.1 cubic meters per minute during the weak stirring stage.

[0055] The tapping temperature of the molten steel is 1500-1560°C. The tapping temperature of the molten steel in this embodiment is 1500°C, and can be set to 1560°C or 1530°C in other embodiments.

[0056] S104, in the die casting stage, the casting ingot mold adopts a 1.1 or 1.7 ton ingot mold, the mold temperature is between 40 and 90°C, the mold temperature in this embodiment is 40°C, and it can be controlled at 90°C or 60°C in other embodiments; the protective slag adopts the bottom laying method; before the end of casting, a high-efficiency heat-generating agent is added to the riser, and the heat-generating agent is evenly dispersed. The die casting adopts an argon protection device, and the pouring process adopts argon protection to prevent secondary oxidation. The standing time after pouring is between 1 and 6 hours. The standing time in this embodiment is one hour, and the standing time in other embodiments is 6 hours or 3 hours.

[0057] S105, 1.7 ton ingot is forged to obtain 180×180 square billet, which is then rolled into wires of various specifications.

[0058] The inclusion rating of the finished wire rods meets the requirements, as shown in Table 1. The mechanical properties of the finished wire rods also meet the requirements, as shown in Table 2.

[0059] Embodiment 2:

[0060] This embodiment is used as a comparative example, which shows an existing old production process of embodiment 1, and the embodiment includes:

[0061] In S201 and EAF rough refining stages, the charge is added in three batches, the tapping temperature is between 1550 and 1650°C, and the Si content of the tapping steel is about 0.10% to 0.40%.

[0062] In the S202 and AOD refining stages, lime is added during the oxidation period, and other alloys are added according to the requirements of the molten steel composition. The temperature at the end of oxygen decarburization is between 1700 and 1720°C; during the pre-reduction period, an aluminum ingot reduction process is adopted, aluminum ingots are added, and part of the slag is removed after the end; during the reduction period, lime and slag-removing agent are added, and aluminum ingots, pure titanium, pure nickel, electrolytic manganese and other alloys are added according to the requirements of the molten steel composition;

[0063] Control the slag composition to 50~60%CaO+20~30%SiO2+5~10%Al2O3+10~20%TiO2+2~5%MgO+5~8%CaF2.

[0064] In the S203 and LF refining stages, argon is blown from the bottom to stir and promote the removal of inclusions; the LF treatment time is not less than 80 minutes; by adding aluminum wire and pure titanium, the content of Al and Ti elements is controlled to meet the target requirements;

[0065] The tapping temperature of molten steel is 1510~1570℃.

[0066] S204, in the mold casting stage, the casting ingot is a φ350 electrode rod ingot, the mold temperature is between 40 and 90°C, and the protective slag is laid on the bottom. The standing time after casting is between 1 and 6 hours.

[0067] S205, electroslag remelting stage: electroslag remelting φ350 electrode rod, raw material length 2.6m, raw material weight 1825kg. The melting rate in the startup stage is about 1.0~7.0kg / min, the melting rate in the smelting stage is about 2.0~10.0kg / min, and the melting rate in the filling stage is graded and degraded. The diameter of the electroslag ingot produced is 435mm, the power consumption per ton of steel is 800~1600 degrees, the argon consumption per ton of steel is 20~100Nm3, the slag consumption per ton of steel is 10~60kg, and the smelting time is 300~600min.

[0068] S206 and φ435 electroslag ingots are forged to obtain 250×250 square billets, which are then rolled to obtain 180×180 square billets, and then rolled to obtain wires of various specifications.

[0069] Embodiment three:

[0070] This embodiment provides a production process control method for a high-aluminum and high-titanium iron-nickel based alloy, which is used to control the production process in the first embodiment. Figure 1 As shown, the specific steps of this method are:

[0071] Step S301, obtaining stirring characteristics during bottom blowing argon stirring in the LF refining process, as well as the stirring time and slag composition of the stirring characteristics.

[0072] During the LF refining process, aluminum wire and pure titanium are added to the molten steel, and argon is blown at the bottom for stirring. The duration of strong argon blowing is recorded as T1. After the duration T1, the amount of argon blown decreases linearly (that is, the gradual weakening mode), and the length of the linear decrease is T2. [T1, T2] is recorded as the stirring feature, and the sum of T1 and T2 is recorded as the stirring time of the stirring feature, that is, the LF treatment time after the addition of aluminum wire and pure titanium.

[0073] The purpose of adding aluminum wire and pure titanium is to control the aluminum and titanium content in the molten steel to meet the target composition requirements; the argon bottom blowing is carried out in a mode of first strong blowing and then gradually weakening, which can not only promote the floating removal of debris such as slag, but also prevent slag rolling and secondary oxidation.

[0074] If T1 and T2 are not set properly during bottom blowing argon stirring, slag entanglement and secondary oxidation cannot be completely prevented.

[0075] At the end of stirring in this embodiment, on the one hand, the molten steel is sampled and tested to obtain the aluminum and titanium content in the molten steel; due to possible slag rolling and secondary oxidation problems, aluminum and titanium will appear in the slag, resulting in the aluminum and titanium content in the molten steel failing to meet the target component requirements. At this time, aluminum wire and pure titanium need to be added to the molten steel again or multiple times; on the other hand, after the stirring is completed, all floating slag and other debris are removed, and the slag is tested to obtain the composition of the slag and the weight of each component; in this embodiment, the slag composition is recorded as the slag composition corresponding to the above-mentioned stirring characteristics.

[0076] Step S302, after adding aluminum and titanium elements, obtain the stirring characteristics F1 when the slag is optimal and the stirring characteristics F2 when the stirring time is minimum according to the amount of aluminum and titanium elements added; the optimal slag refers to the time when the aluminum and titanium content in the slag is the minimum.

[0077] In the LF refining process, due to the problems of slag rolling and secondary oxidation, adding aluminum wire and pure titanium only once may not make the aluminum and titanium content in the molten steel meet the target composition. In order to obtain molten steel that meets the target composition, it is necessary to add aluminum wire and pure titanium multiple times. The stirring feature F1 when the slag is optimal describes: when the bottom blowing argon is stirred, the stirring feature required to minimize the amount of aluminum and titanium in the slag. This stirring feature can avoid slag rolling and secondary oxidation problems as much as possible, so that after adding aluminum wire and pure titanium once or a few times, the aluminum and titanium content in the molten steel can meet the target composition requirements. The stirring feature F2 when the stirring time is the smallest describes: the stirring feature used when the stirring time consumed is the smallest or the LF processing efficiency is maximized.

[0078] As an example, a method for obtaining the stirring feature F1 and the stirring feature F2 according to the amount of added aluminum and titanium elements includes:

[0079] In each historical LF refining process, the amount of aluminum and titanium elements added each time aluminum wire and pure titanium are added is recorded, and the stirring characteristics used after adding the aluminum wire and pure titanium, as well as the stirring time of the stirring characteristics and the slag composition corresponding to the stirring characteristics are recorded; the amount of aluminum and titanium elements added, the stirring characteristics, the stirring time of the stirring characteristics and the slag composition corresponding to the stirring characteristics recorded each time are recorded as a historical record, and all historical records of all historical LF refining processes are stored in the MySql database.

[0080] For the ongoing LF refining process, the weight of the aluminum and titanium elements added when adding aluminum wire and pure titanium is obtained. In the historical records, several historical records with the smallest difference from the weight are obtained and recorded as reference records. The several records in this embodiment refer to 20% of all historical records (rounded off).

[0081] Among these reference records, a reference record with the smallest amount of aluminum and titanium elements in the slag is obtained, and the stirring characteristics contained in this reference record are used as stirring feature F1; among these reference records, a reference record with the smallest stirring time is obtained, and the stirring characteristics contained in this reference record are used as stirring feature F2.

[0082] As another example, a method for obtaining the stirring feature F1 and the stirring feature F2 according to the amount of added aluminum and titanium elements includes:

[0083] In the reference records, several reference records (for example, 10) in which the amount of aluminum and titanium elements in the slag is the smallest are obtained, and the mean of the stirring characteristics of these reference records is recorded as the stirring feature F1. In other embodiments, the stirring characteristics of these reference records can also be clustered by mean shift, and the mean of the stirring characteristics in the category with the highest density is recorded as the stirring feature F1.

[0084] In this example, the slag composition corresponding to the stirring feature F1 is: the slag composition corresponding to the stirring feature that is the smallest different from (ie, the closest to) the stirring feature F1.

[0085] In addition, for the aluminum and titanium content (mass percentage) in the slag included in these reference records, the reference records whose aluminum and titanium content is less than the preset threshold th1 are obtained, and the stirring feature with the minimum stirring time in the reference records whose aluminum and titanium content is less than the preset threshold th1 is used as the stirring feature F2. In this embodiment, the preset threshold th1 corresponding to aluminum is 0.3%, and the preset threshold th1 corresponding to titanium is 2%.

[0086] It should be noted that, during the first five LF refining processes, the value range of T2 is [20 minutes, 60 minutes], and the value range of T1 is [40 minutes, 80 minutes]. Specifically, in this embodiment, during the first five LF refining processes, T2 is randomly selected within [20 minutes, 60 minutes], and T1 is selected within [40 minutes, 80 minutes]. If the sum of T1 and T2 is less than 80 minutes, T1 and T2 are re-obtained.

[0087] The ongoing LF refining process described above in this embodiment refers to the LF refining process after the first five LF refining processes. In other embodiments, 5 may be replaced by other values, such as 10 or 15, which is not specifically limited in this embodiment.

[0088] Step S303: Obtain the first stirring feature and the second stirring feature corresponding to the stirring feature F1 and the stirring feature F2.

[0089] In this embodiment, in order to prevent obvious slag rolling and secondary oxidation problems and to speed up the efficiency of the entire LF refining process, it is necessary to obtain more appropriate stirring characteristics, and at the same time, it is necessary to ensure that the LF refining process does not take too long to stir and avoid multiple additions of aluminum wire and pure titanium.

[0090] For the stirring feature F1, the slag corresponding to the stirring feature F1 is obtained to be Q. The more aluminum and titanium elements there are in Q, the more seriously the added aluminum and titanium elements are affected by slag rolling and secondary oxidation. For example, the aluminum and titanium elements are secondary oxidized into slag and other impurities or are adsorbed by the slag rolled into the molten steel. This ultimately leads to a large difference between the aluminum and titanium content in the molten steel and the target content, and thus a greater need for additional addition of aluminum wire and pure titanium.

[0091] This embodiment obtains the stirring characteristics when the slag is optimal and the stirring characteristics when the stirring time is minimum according to the aluminum and titanium elements in Q, and records them as the first stirring characteristics and the second stirring characteristics of the stirring characteristic F1 respectively. The specific process is the same as step S002.

[0092] The first stirring feature of stirring feature F1 describes the stirring feature required to minimize the aluminum and titanium elements in the slag again after adding aluminum wire and pure titanium again when stirring with stirring feature F1. When stirring feature F1 and the first stirring feature of stirring feature F1 are used for the current stirring and the next stirring, the aluminum and titanium elements in the slag can be reduced as much as possible (i.e., slag rolling and secondary oxidation can be further prevented), and then aluminum wire and pure titanium do not need to be added multiple times in the future. The second stirring feature of stirring feature F1 describes the stirring feature required to quickly complete the stirring and reduce the LF processing time after adding aluminum wire and pure titanium again.

[0093] Furthermore, for the stirring feature F2, the slag composition Q corresponding to the stirring feature F1 is obtained, and the stirring characteristics when the slag is optimal and the stirring characteristics when the stirring time is minimum are obtained according to the amount of aluminum and titanium elements in the slag composition Q, and they are respectively recorded as the first stirring characteristic and the second stirring characteristic of the stirring feature F2. The specific process is the same as step S002.

[0094] The first stirring feature of stirring feature F2 describes the stirring feature required to minimize the aluminum and titanium elements in the slag again after adding aluminum wire and pure titanium again when stirring with stirring feature F2. When stirring feature F2 and the first stirring feature of stirring feature F2 are used for the current stirring and the next stirring, the current LF processing time can be reduced and the aluminum and titanium elements in the slag can be reduced as much as possible during the next stirring (that is, further preventing slag rolling and secondary oxidation), thereby taking into account the LF processing time while reducing the number of subsequent additions of aluminum wire and pure titanium, so that the LF refining process can be carried out efficiently. The second stirring feature of stirring feature F2 describes that stirring is completed quickly after adding aluminum wire and pure titanium again; when stirring feature F2 and the second stirring feature of stirring feature F2 are used for the current stirring and the next stirring, the LF processing time can be further reduced as much as possible, and the LF refining efficiency can be improved.

[0095] It should be noted that when the aluminum and titanium content in the slag component Q is equal to 0 or close to 0 (for example, when the aluminum and titanium content is less than 0.1% and 0.7%), it means that the weight of aluminum wire and pure titanium added next time is 0, that is, no aluminum wire and pure titanium will be added, and steel can be tapped when the molten steel meets the tapping temperature.

[0096] So far, the first stirring feature and the second stirring feature of the stirring feature F1 and the first stirring feature and the second stirring feature of the stirring feature F2 are acquired.

[0097] Step S304 , obtaining a supplementary stirring feature of the stirring feature F1 and a supplementary stirring feature of the stirring feature F2 according to the stirring feature F1 and the first stirring feature and the second stirring feature corresponding to the stirring feature F2 .

[0098] The additional stirring feature of stirring feature F1 and the additional stirring feature of stirring feature F2 describe: in order to prevent slag rolling and secondary oxidation and shorten the stirring time (that is, shorten the LF processing time), when stirring, the stirring conditions existing when aluminum wire and pure titanium are added for the previous time and when aluminum wire and pure titanium are added for the next time, including the slag difference and time consumption caused by stirring.

[0099] As an example, the method for obtaining the additional stirring feature of the stirring feature F1 is:

[0100] The aluminum and titanium content in the slag composition corresponding to the stirring feature F1 is recorded as fa1, and the aluminum and titanium content in the slag composition corresponding to the first stirring feature of the stirring feature F1 is recorded as fb1; the sum of the stirring time of the stirring feature F1 and the stirring time of the second stirring feature of the stirring feature F1 is recorded as t1, and the supplementary stirring characteristic of the stirring feature F1 is [slag difference fa1-fb1, time consumption t1].

[0101] It should be noted that when the current stirring and the next stirring are performed with the stirring feature F1 and the first stirring feature of the stirring feature F1, slag entanglement and secondary oxidation can be further prevented. The greater the slag difference, the more obvious the slag change, that is, the slag entanglement and secondary oxidation problems are significantly solved. When the current stirring and the next stirring are performed with the stirring feature F1 and the second stirring feature of the stirring feature F1, slag entanglement and secondary oxidation can be prevented while consuming as little time as possible during the subsequent stirring after the aluminum and titanium are added. The less time consumption, the less time consumption, indicating that slag entanglement and secondary oxidation can be prevented to a certain extent, and the stirring time after the subsequent aluminum and titanium are added is less.

[0102] The method for obtaining the additional stirring feature of the stirring feature F2 is:

[0103] The amount of aluminum and titanium elements in the slag composition corresponding to the stirring feature F2 is recorded as fa2, and the amount of aluminum and titanium elements in the slag composition corresponding to the second stirring feature of the stirring feature F2 is recorded as fb2; the sum of the stirring time of the stirring feature F2 and the stirring time of the first stirring feature of the stirring feature F2 is recorded as t2, and the supplementary stirring characteristic of the stirring feature F2 is: [slag difference fa2-fb2, time consumption t2].

[0104] It should be noted that when the current stirring and the next stirring are performed with stirring feature F2 and the second stirring feature of stirring feature F2, the LF processing time can be further reduced. The greater the slag difference, the more obvious the slag change, that is, while reducing the LF processing time, slag entanglement and secondary oxidation can also be prevented. When the current stirring and the next stirring are performed with stirring feature F2 and the first stirring feature of stirring feature F2, the LF processing time can be reduced while avoiding to a certain extent the problems of slag entanglement and secondary oxidation during the subsequent stirring after adding aluminum and titanium elements; the smaller the time consumption, the shorter the stirring time after aluminum and titanium, and the problems of slag entanglement and secondary oxidation during the subsequent stirring after adding aluminum and titanium elements can also be avoided to a certain extent.

[0105] Step S305 , the additional stirring characteristics of the stirring characteristics F1 and the additional stirring characteristics of the stirring characteristics F2 are combined to obtain the final stirring characteristics, wherein the final stirring characteristics are the stirring characteristics when argon is blown at the bottom after the aluminum element and the titanium element are added.

[0106] The additional stirring feature of the stirring feature F1 in this embodiment and the additional stirring feature of the stirring feature F2 obtain the final stirring feature, and the stirring conditions required for the current additional addition of aluminum wire and pure titanium and the next additional addition of aluminum wire and pure titanium can be combined to obtain a new stirring feature (that is, the final stirring feature), thereby avoiding the problem of multiple additional additions of aluminum wire and pure titanium and excessive time consumption caused by slag entrainment and secondary oxidation problems, or avoiding the problem of deviation of the composition of the molten steel from the target content and low refining efficiency caused by slag entrainment and secondary oxidation problems, thereby ensuring the production efficiency and production quality of the high-aluminum and high-titanium iron-nickel-based alloy.

[0107] As an example, the method for obtaining the final stirring feature includes:

[0108] The reference coefficient of the stirring feature F1 is obtained, and the reference coefficient of the stirring feature F1 is positively correlated with the slag difference of the stirring feature F1, and the reference coefficient of the stirring feature F1 is negatively correlated with the time consumption of the stirring feature F1.

[0109] The reference coefficient of the stirring feature F2 is obtained. The reference coefficient of the stirring feature F2 is positively correlated with the slag difference of the stirring feature F2, and the reference coefficient of the stirring feature F2 is negatively correlated with the time consumption of the stirring feature F2.

[0110] The larger the reference coefficient is, the more it means that when stirring with stirring feature F1 or stirring feature F2, when aluminum wire or pure titanium needs to be added again later, the refining efficiency can be improved in terms of reducing the aluminum and titanium content in the slag and shortening the stirring time. That is, the stirring feature F1 or stirring feature F2 can be used as the stirring feature during current stirring.

[0111] The final stirring characteristic is obtained according to the reference coefficient of the stirring characteristic F1 and the reference coefficient of the stirring characteristic F2.

[0112] As an example, the final stirring feature is obtained according to the reference coefficient of the stirring feature F1 and the reference coefficient of the stirring feature F2, including the method as follows: if the reference coefficient of the stirring feature F1 is greater than or equal to the reference coefficient of the stirring feature F2, the stirring feature F1 is used as the final stirring feature; if the reference coefficient of the stirring feature F1 is less than the reference coefficient of the stirring feature F2, the stirring feature F2 is used as the final stirring feature.

[0113] As a preferred example, the final stirring feature is obtained according to the reference coefficient of the stirring feature F1 and the reference coefficient of the stirring feature F2, including the method of:

[0114] The final mixing characteristics ,in , They respectively represent the reference coefficient of the stirring feature F1 and the reference coefficient of the stirring feature F2.

[0115] In this example, the stirring features F1 and F2 are integrated, so that after the current addition of aluminum wire and pure titanium, not only can the problems of slag entrainment and secondary oxidation be avoided as much as possible while the stirring efficiency is improved, but also the number of subsequent additions of aluminum wire and pure titanium can be reduced as much as possible, and the stirring efficiency is also high, thereby avoiding the deviation of the composition of the molten steel from the target content caused by the problems of slag entrainment and secondary oxidation and further improving the refining efficiency.

[0116] In addition, each time aluminum wire and pure titanium are added, the final stirring characteristics are obtained according to this example, so that the historical records stored in the database can gradually increase and include more accurate stirring characteristics, so that the stirring characteristics F1 and F2 obtained from the database next time are more reliable.

[0117] As an optional example, a method for obtaining the reference coefficient of the stirring feature F1 and the reference coefficient of the stirring feature F2 includes:

[0118] The ratio of the slag difference of the stirring feature F1 to the time consumption of the stirring feature F1 is recorded as the reference coefficient of the stirring feature F1. The ratio of the slag difference of the stirring feature F2 to the time consumption of the stirring feature F2 is recorded as the reference coefficient of the stirring feature F1.

[0119] As a preferred example, the method for obtaining the reference coefficient of the stirring feature F1 and the reference coefficient of the stirring feature F2 includes:

[0120] For the current LF refining process, aluminum wire and pure titanium have been added several times in this process, and the number of additions is recorded as n. If aluminum wire and pure titanium have not been added, n=0.5; in addition, the duration of the current LF refining is recorded as tt. If refining has just started, tt=1.

[0121] The ratio of the slag difference of the stirring feature F2 or F1 to n is recorded as the first ratio, the product of the time consumption of the stirring feature F2 or F1 and tt is recorded as the first product, and the reference coefficient of the stirring feature F2 or F1 is the ratio of the first ratio to the first product.

[0122] In this example, the additional stirring feature is corrected by the refining conditions of the refining process that has been carried out. Specifically, when n is larger, it means that multiple additions have been made. At this time, the first ratio is smaller, which can ensure that the reference coefficient obtained by this preferred example is smaller than the reference coefficient obtained by the optional example. That is, based on the multiple additions of aluminum wire and pure titanium, this preferred example pays less attention to the difference changes of aluminum and titanium elements in the slag in the subsequent refining process, but pays relatively more attention to the consumption of stirring time; when n is smaller, it means that multiple additions of aluminum wire and pure titanium have not been made, or aluminum wire and pure titanium have just been added. At this time, the first ratio is larger, which can ensure that the reference coefficient obtained by this preferred example is larger than the reference coefficient obtained by the optional example. That is, in the subsequent refining process, this preferred example pays more attention to the difference changes of aluminum and titanium elements in the slag, and relatively less attention to the consumption of stirring time.

[0123] Similarly, the larger tt is, the longer the LF out-of-furnace refining process has lasted (or more time has been spent on argon bottom blowing and stirring). At this time, the first product is larger, which can ensure that the reference coefficient obtained by this preferred example is smaller than the reference coefficient obtained by the optional example. That is, when the refining time has lasted for a long time, the subsequent refining process pays less attention to the differential changes of aluminum and titanium elements in the slag, but pays relatively more attention to the reduction of stirring time consumption; when tt is smaller, it means that less time has been spent on argon bottom blowing and stirring. At this time, the first product is smaller, which can ensure that the reference coefficient obtained by this preferred example is larger than the reference coefficient obtained by the optional example. That is, the subsequent refining process of this preferred example pays more attention to the differential changes of aluminum and titanium elements in the slag, and relatively less attention to the consumption of stirring time.

[0124] It should be noted that, in order to be consistent with the dimensions and orders of magnitude of the above optional examples, in other embodiments, the first product can be equal to: the product of the time consumption of the stirring feature F2 and tt divided by the time t0, where t0 is equal to the mean stirring time of all stirring processes.

[0125] In this preferred example, the additional stirring characteristics are corrected by the refining conditions of the refining process that has been carried out (i.e., n and tt are introduced), and combined with the stirring conditions when aluminum wire and pure titanium are added next time (i.e., the additional stirring characteristics), the two current stirring characteristics (i.e., stirring characteristics F1 and F2) are merged, thereby further preventing slag rolling and secondary oxidation, and improving the LF out-of-furnace refining efficiency.

[0126] For all the above embodiments, the inclusion ratings of the finished wires produced in Embodiments 1 and 3 meet the requirements, as shown in Table 1;

[0127] It shows the ratings of Class A, Class B, Class C, and Class D inclusions in both coarse and fine sizes. In Table 1, the minimum rating is 0.0 and the maximum rating is 2.0. The lower the rating, the higher the purity and better the quality of the steel.

[0128] Class A inclusions refer to sulfide inclusions, such as manganese sulfide, etc.; Class B inclusions refer to alumina inclusions, including other aluminum oxides; Class C inclusions refer to silicate inclusions, such as calcium silicate and manganese silicate; Class D inclusions refer to spherical non-deformed oxide inclusions. The difference in inclusion levels between Examples 1 and 3 and the comparative example (ie, Example 2) is not large. Class D inclusions are more serious in the non-electroslag remelting process, but the TiN inclusion level reaches the level of the electroslag remelting process.

[0129] The mechanical properties of the finished wires produced in Examples 1 and 3 meet the requirements, as shown in Table 2; in Table 2, Rm, A, and Z are commonly used to describe the mechanical properties of materials, representing tensile strength, elongation after fracture, and cross-sectional shrinkage, respectively.

[0130] The mechanical properties of Examples 1 and 3 and the comparative example (ie, Example 2) are similar, but there are differences in the mechanical properties of the wires produced from the head and tail of the electroslag ingot by the electroslag remelting process.

[0131] Tables 3 and 4 show the element contents of the head and tail of the electroslag ingot and the ingot, respectively. The composition of the head and tail of the electroslag ingot is quite different, especially the aluminum content; however, the composition difference between the head and tail of the ingot is relatively small. Therefore, through the above experimental comparison, it can be seen that the production method of a high-aluminum and high-titanium iron-nickel-based alloy provided by the present invention without electroslag remelting and the control method based on the production method reduce the production cost while ensuring product quality.

[0132] Table 1. Comparison of cleanliness of finished alloy wires of Examples 1 and 3 and that of finished alloy wire of Example 2.

[0133]

[0134] Table 2. Comparison of mechanical properties of the finished alloy wires of Examples 1 and 3 and the finished alloy wire of Example 2.

[0135]

[0136] Table 3. Differences in composition between the head and tail of the electroslag ingot of Example 2 (i.e., the old process of the comparative example) (mass percentage, %).

[0137]

[0138] Table 4. Differences in composition between the head and tail of the ingots of Examples 1 and 3 (i.e., the new process) (mass percentage, %).

[0139]

[0140] The above description is only a preferred embodiment of the present invention and is not intended to limit the present invention. Any modifications, equivalent substitutions, improvements, etc. made within the principles of the present invention should be included in the protection scope of the present invention.

Claims

1. A production process control method for high-aluminum and high-titanium iron-nickel based alloy, characterized in that: The production process in the method includes EAF roughing, AOD refining, LF refining and die casting; during the LF refining, aluminum and titanium elements are added to the molten steel, and when argon is blown at the bottom for stirring, after blowing argon for a time length of T1, the blowing amount of argon decreases linearly, and the length of the linear decrease time is T2; T1 and T2 are recorded as stirring characteristics, and the sum of T1 and T2 is recorded as the stirring time of the stirring characteristic, and at the end of the stirring, the slag is sampled and tested to obtain the slag composition corresponding to the stirring characteristic; After adding aluminum and titanium elements, the stirring characteristics F1 when the slag is optimal and the stirring characteristics F2 when the stirring time is minimum are obtained according to the amount of aluminum and titanium elements added; the optimal slag refers to the time when the aluminum and titanium content in the slag is the minimum; For any stirring feature F in F1 and F2, the slag composition corresponding to the stirring feature F is recorded as Q; According to the amount of aluminum and titanium elements in the slag component Q, the stirring characteristic when the slag is optimal and the stirring characteristic when the stirring time is minimum are obtained, and they are recorded as the first stirring characteristic and the second stirring characteristic of the stirring characteristic F respectively; The difference between the slag composition corresponding to the stirring feature F1 and the slag composition corresponding to the first stirring feature of the stirring feature F1, and the sum of the stirring time of the stirring feature F1 and the stirring time of the second stirring feature of the stirring feature F1 are recorded as the supplementary stirring feature of the stirring feature F1; The difference between the slag composition corresponding to the stirring feature F2 and the slag composition corresponding to the second stirring feature of the stirring feature F2, and the sum of the stirring time of the stirring feature F2 and the stirring time of the first stirring feature of the stirring feature F2 are recorded as the additional stirring feature of the stirring feature F2; The final stirring characteristic is obtained according to the supplementary stirring characteristic of the stirring characteristic F1 and the supplementary stirring characteristic of the stirring characteristic F2, and the final stirring characteristic is the stirring characteristic when argon is blown at the bottom after adding the aluminum and titanium elements.

2. The production process control method of a high-aluminum and high-titanium iron-nickel based alloy according to claim 1, characterized in that: The specific steps for obtaining the additional stirring feature of the stirring feature F1 and the additional stirring feature of the stirring feature F2 are as follows: The amount of aluminum and titanium in the slag composition corresponding to the stirring feature F1 is recorded as fa1, and the amount of aluminum and titanium in the slag composition corresponding to the first stirring feature of the stirring feature F1 is recorded as fb1; the sum of the stirring time of the stirring feature F1 and the stirring time of the second stirring feature of the stirring feature F1 is recorded as t1, and the additional stirring feature of the stirring feature F1 includes: slag difference fa1-fb1, time consumption t1; The amount of aluminum and titanium elements in the slag composition corresponding to the stirring feature F2 is recorded as fa2, and the amount of aluminum and titanium elements in the slag composition corresponding to the second stirring feature of the stirring feature F2 is recorded as fb2; the sum of the stirring time of the stirring feature F2 and the stirring time of the first stirring feature of the stirring feature F2 is recorded as t2, and the supplementary stirring characteristics of the stirring feature F2 include: slag difference fa2-fb2, and time consumption t2.

3. The production process control method of a high-aluminum and high-titanium iron-nickel based alloy according to claim 1, characterized in that: The method of obtaining the final stirring feature according to the additional stirring feature of the stirring feature F1 and the additional stirring feature of the stirring feature F2 includes the following specific steps: Obtaining a reference coefficient of the stirring feature F1, wherein the reference coefficient of the stirring feature F1 is positively correlated with the slag difference of the stirring feature F1, and the reference coefficient of the stirring feature F1 is negatively correlated with the time consumption of the stirring feature F1; Obtaining a reference coefficient of the stirring feature F2, wherein the reference coefficient of the stirring feature F2 is positively correlated with the slag difference of the stirring feature F2, and the reference coefficient of the stirring feature F2 is negatively correlated with the time consumption of the stirring feature F2; Final mixing characteristics Wherein w1 and w2 represent the reference coefficient of the stirring feature F1 and the reference coefficient of the stirring feature F2 respectively.

4. The production process control method of a high-aluminum and high-titanium iron-nickel based alloy according to claim 3, characterized in that: The specific steps of obtaining the reference coefficient of the stirring feature F1 and the reference coefficient of the stirring feature F2 are as follows: Aluminum and titanium elements have been added several times during the LF refining process, the number of times the aluminum and titanium elements have been added is recorded as n, and the duration of LF refining is recorded as tt; for any stirring feature F in F1 and F2, the ratio of the slag difference of the stirring feature F to n is recorded as the first ratio, the product of the time consumption of the stirring feature F and tt is recorded as the first product, and the reference coefficient of the stirring feature F is equal to the ratio of the first ratio to the first product.

5. The production process control method of a high-aluminum and high-titanium iron-nickel based alloy according to claim 1, characterized in that: The method of obtaining the optimal stirring characteristic F1 of the slag according to the amount of added aluminum and titanium elements, and the stirring characteristic F2 when the stirring time is the smallest, comprises the following specific steps: During each LF refining process in history, the weight of aluminum and titanium elements added each time, the stirring feature used, the stirring time of the stirring feature, and the slag composition corresponding to the stirring feature are recorded as a historical record; For the ongoing LF refining process, the weight of the added aluminum and titanium elements is obtained and recorded as the first weight. In the historical records, several historical records with the smallest difference from the first weight are obtained and recorded as reference records. A reference record with the smallest aluminum and titanium content in the slag composition is obtained from the reference records, and the stirring characteristics contained in the reference record with the smallest aluminum and titanium content are used as the stirring feature F1; a reference record with the smallest stirring time is obtained from the reference records, and the stirring characteristics contained in the reference record with the smallest stirring time are used as the stirring feature F2.

6. The production process control method of a high-aluminum and high-titanium iron-nickel based alloy according to claim 1, characterized in that: The chemical composition of the high-aluminum and high-titanium iron-nickel based alloy is as follows by mass percentage: C≤0.08%, Si≤1%, Mn≤3%, P≤0.03%, S≤0.02%, Cr: 13.5%-16%, Ni: 24%-27%, Mo: 1%-1.5%, Al≤0.35%, Ti: 1.9%-2.35%, B: 0.001%-0.01%, and the remaining elements are Fe.

7. The production process control method of a high-aluminum and high-titanium iron-nickel based alloy according to claim 1, characterized in that: In the EAF rough refining stage, the tapping temperature is controlled between 1550 and 1650°C, and the Si content of the tapping steel is controlled between 0.1% and 0.4%.

8. The production process control method of a high-aluminum and high-titanium iron-nickel based alloy according to claim 1, characterized in that: In the AOD refining stage, lime is added during the oxidation period, and the temperature is controlled at 1680-1720℃ at the end of oxygen decarburization; during the pre-reduction period, ferrosilicon reduction technology is adopted, ferrosilicon and slag-removing agent are added, and the slag basicity is controlled to be greater than 1.

5. After the end, the slag is scraped off; during the reduction period, lime and slag-removing agent are added, and aluminum ingots and pure titanium are added; The slag composition is controlled to 50-60% CaO + 20-25% SiO2 + 10-20% Al2O3 + 6-12% TiO2 + 2-5% MgO + 5-12% CaF2.

9. The production process control method of a high-aluminum and high-titanium iron-nickel based alloy according to claim 1, characterized in that: In the LF refining stage, T2 is not less than 20 minutes, and the stirring time of the stirring characteristic is not less than 80 minutes; the steel liquid tapping temperature is controlled at 1500-1560℃.

10. The production process control method of a high-aluminum and high-titanium iron-nickel based alloy according to claim 1, characterized in that: During the die casting stage, the mold temperature is controlled between 40 and 90°C; the protective slag is protected by the bottom laying method, and a high-efficiency heating agent is added to the riser before the end of casting, and the heating agent is evenly dispersed; argon gas protection is used for die casting and argon gas protection is used during the pouring process.

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