CN113444976B - High-carbon high-aluminum steel for drilling and lock making and preparation method thereof - Google Patents
High-carbon high-aluminum steel for drilling and lock making and preparation method thereof Download PDFInfo
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- C21D1/18—Hardening; Quenching with or without subsequent tempering
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
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Abstract
The invention discloses high-carbon high-aluminum steel for drilling and lock making and a preparation method thereof, and belongs to the technical field of locks. The high-carbon high-aluminum steel comprises the following chemical components in percentage by mass: c: 1% -1.5%, Si: 0.3% -0.6%, Mn: 0.2% -0.6%, P: 0.01% -0.04%, S: 0.02% -0.04%, Bi: 0.03-0.06%, Al: 1.5% -2.5%, N: 0.003-0.006 percent of Ti: 0-0.03 percent, the balance of Fe and inevitable impurities, and Si + Al in the components is controlled to be more than or equal to 2.4 percent. The preparation process comprises the following steps: smelting and casting the materials into ingots according to the set chemical components, forging the ingots into billets after high-temperature homogenization treatment, and performing hot rolling, heat preservation, quenching, tempering and shot blasting treatment on the billets to obtain ferrite structures with low hardness and a large amount of graphite particles of 1-10 mu m uniformly distributed. The preparation method of the high-carbon high-aluminum steel conforms to the casting and rolling integrated process conditions, can realize continuous large-scale production, has the drilling performance meeting the continuous drilling processing requirement, and can replace the conventional HT200 grey cast iron lock body material.
Description
Technical Field
The invention relates to the technical field of locks, in particular to high-carbon high-aluminum steel for drilling and lock making and a preparation method thereof.
Background
Padlocks are the oldest and bulky families of locks, and other locks are derived and spawned from the class of padlocks. Zhejiang Pu Jiang county is the largest area where padlocks and gourd locks are produced and sold in China at present, and the quantity of the padlocks and the gourd locks produced in each year exceeds 30 million tons. The lock body is mainly divided into a stainless steel lock, a copper lock, an iron lock and a zinc alloy lock according to the material, wherein the iron lock body has the most common use due to low price and good drilling processability, so that the yield is also the largest.
At present, the iron lock bodies on the market are mainly made of HT200 grey cast iron, and the main reason is that a large amount of graphite particles with lubricating and stress concentration source functions in the grey cast iron can ensure that the materials have good drilling processability. Although the grey cast iron has excellent drilling processability, the grey cast iron has low plasticity and toughness and is difficult to forge and roll, so that the grey cast iron is mainly produced by adopting induction furnace smelting and die casting molding, and the process not only consumes a large amount of electric power, but also has low production efficiency and great environmental pollution.
The national invention patents with publication numbers of CN101899555A, CN101906597A, CN106947907A and CN107904377A obtain a high proportion of graphite particles by optimizing alloy element components and rolling and heat treatment processes, successfully prepare the graphite free-cutting steel with excellent cutting performance and cold and hot forming performance, but the steel has higher hardness and smaller size of graphite particles in free-cutting phase stones in the steel, has the characteristics of large resistance, slow chip removal, fast temperature rise of a drill bit and the like when high-speed drilling is carried out, cannot meet the continuous drilling processing requirements of padlocks or gourd locks, and needs further improvement.
Disclosure of Invention
1. Technical problem to be solved by the invention
Based on the fact that the grey cast iron in the prior art has a large amount of spherical or flake graphite, the grey cast iron has the advantages of small resistance, fast chip removal, fast heat dissipation and small abrasion to a drill bit in the drilling process, however, the grey cast iron has poor plasticity and toughness due to high carbon content, and therefore small-scale production can be carried out only through a die casting forming process in the prior art. The invention provides high-carbon high-aluminum steel for drilling and lock making, which can realize cast-rolling integrated large-scale production, has the characteristics of small drilling resistance, quick chip removal, long service life of a drill bit and the like during drilling and machining, and can realize continuous drilling and cutting machining production of lock bodies such as padlocks, gourd locks and the like.
2. Technical scheme
In order to achieve the purpose, the technical scheme provided by the invention is as follows:
the invention relates to high-carbon high-aluminum steel for drilling and lock making, which comprises the following chemical components in percentage by mass: c: 1% -1.5%, Si: 0.3% -0.6%, Mn: 0.2% -0.6%, P: 0.01% -0.04%, S: 0.02% -0.04%, Bi: 0.03-0.06%, Al: 1.5% -2.5%, N: 0.003-0.006 percent of Ti: 0-0.03 percent, the balance of Fe and inevitable impurities, and Si + Al in the components is controlled to be more than or equal to 2.4 percent.
The action mechanism of the main elements in the steel in the invention is as follows:
the C is a main source of graphite in the steel for the lock body, and has the main function that the graphite is converted into the graphite through allotype during graphitization heat treatment, so that the purpose of improving the drilling processability is achieved. When the content of C in the steel is low, the graphitization heat treatment time is long, the graphite content is low, the effects on the lubrication and stress concentration source of the steel are not obvious, and the drilling processability of the steel is not high; when the content of C is higher, the plasticity and the toughness of the steel are reduced, and the solubility of the easy-drilling element Bi in the steel is reduced.
Si is a non-carbide forming element, has small affinity with C atoms, can obviously inhibit the precipitation of cementite during graphite heat treatment, and is a strong solid solution strengthening element which can increase the strength of steel after the graphitization heat treatment, but the high content of Si can cause the over-high hardness of the steel and is not beneficial to drilling processing, so the content of Si in the steel for locks needs to be strictly controlled.
The Al content of the steel for the lock body is higher, namely 1.5-2.5 percent. Al is insoluble in cementite, can also obviously inhibit the precipitation of the cementite during graphite heat treatment, and simultaneously Al is a solid solution strengthening element and can make up for the deficiency of the strength of the obtained structure ferrite and graphite after complete graphitization. In addition, AlN, formed by combining Al with N in steel, may serve as a nucleation core of graphite to accelerate the graphitization process due to the same simple hexagonal lattice as graphite.
Mn is a conventional alloy element in steel, can expand an austenite phase region and refine ferrite grains, improves the strength and toughness of a steel plate, and can also strengthen the ferrite through solid solution and increase the hardenability. In addition, the solubility of the free-cutting phase Bi in the steel increases with the manganese content in the steel.
Bi mainly plays roles of lubrication and melting embrittlement in steel for lock bodies, so that drill cuttings can be broken and discharged more easily, the heat dissipation speed of a drill in a high-speed drilling process is improved, the service life of the drill is prolonged, but Bi is segregated in a grain boundary, so that the thermoplasticity of the steel is reduced, and rolling cracks are easy to occur. In addition, the solubility of the free-cutting phase Bi in the steel increases with the Mn content in the steel and decreases with the C content in the steel.
Ti can be combined with C in steel at high temperature to form a fine TiC precipitated phase, so that the movement of a grain boundary is hindered, the growth of austenite grains is inhibited, and the thermoplasticity of the steel for the lock body is improved, thereby avoiding the cracking of the steel in the continuous casting and rolling processes.
N can be combined with Al in the steel at high temperature to form a fine AlN precipitated phase, so that the movement of a grain boundary is hindered, the growth of austenite grains is inhibited, and the thermoplasticity of the steel for the lock body is improved, thereby avoiding the cracking of the steel in the continuous casting and rolling processes. In addition, the formed AlN may serve as a nucleation core for graphite to accelerate the graphitization process.
The invention relates to a preparation method of high-carbon high-aluminum steel for drilling and lock making, which comprises the following steps:
step one, smelting by adopting a vacuum induction furnace, and casting into a steel ingot;
step two, forging the cast steel ingot to obtain a steel billet;
step three, carrying out hot rolling on the steel billet;
step four, rolling the steel billet in Accm-50～AccmKeeping the temperature in a muffle furnace at +50 ℃ for 20min, and quickly putting the muffle furnace into water to quench the muffle furnace to room temperature so as to promote complete martensite;
fifthly, putting the quenched steel billet into a muffle furnace at 650-720 ℃ for heat preservation for 2-5 h for tempering;
and sixthly, removing an oxide layer on the surface of the billet through shot blasting to obtain the high-carbon high-aluminum steel.
As a further improvement of the invention, the quenching temperature in the fourth step is Accm-50～Accm℃。
As a further improvement of the invention, in the fifth step, the tempering temperature is 680-710 ℃, and the tempering time is 2-3 hours.
In the second step, the heating temperature of the cast ingot is 1150 ℃, the holding time is 1.5h, and the forged billet has the size of 100mm × 120mm × L.
As a further improvement of the invention, in the third step, the initial rolling temperature of the billet is 1150 ℃, and the final rolling temperature is 900-930 ℃.
As a further improvement of the invention, in the third step, the initial thickness of the initial rolling of the billet is 100mm, and the rolling pass is 6; the final thickness was 26 mm.
3. Advantageous effects
Compared with the prior art, the technical scheme provided by the invention has the following remarkable effects:
(1) according to the high-carbon high-aluminum steel for drilling and lock making, disclosed by the invention, by optimizing each component of the high-carbon high-aluminum steel, on the basis of ensuring the strength of the steel, the precipitation of cementite during graphite heat treatment is inhibited by controlling the contents of Si and Al, and the effective graphitization is ensured; in addition, AlN formed by combining Al with N in the steel has the same simple hexagonal lattice with graphite, and can be used as a nucleation core of the graphite to accelerate the graphitization process, so that the high-carbon high-aluminum steel is ensured to have higher chip removal and chip breaking capacity in the drilling process.
(2) According to the preparation method of the high-carbon high-aluminum steel for drilling and locking, disclosed by the invention, the high-efficiency graphitization of carbon in the high-carbon steel is realized by optimizing an alloy system and quenching and tempering processes, and a small amount of Bi free cutting phase is introduced, so that the hardness of the steel is obviously reduced, and the chip removal and breaking capacity and the heat dissipation speed of a drill bit in the drilling process are improved;
(3) the invention relates to a preparation method of high-carbon high-aluminum steel for drilling and locking, which is characterized in that a rolled steel billet is arranged at Accm-50～AccmKeeping the temperature in a muffle furnace at +50 ℃ for 20min, on one hand, promoting the nucleation and growth of austenite recrystallization grains in the hot rolled plate, on the other hand, reducing the defect density of the deformed hot rolled plate and improving the uniformity of the transverse and longitudinal structures of the deformed hot rolled plate; if the austenitizing temperature is too high and the heat preservation time is too long, the defect density and strain energy in the hot rolled plate are released too much, so that austenite grains are coarser, and the nucleation and growth of graphite grains in the subsequent tempering process are not facilitated; after the heat preservation time is reached, the steel billet is quickly put into water to be quenched to room temperature so as to promote complete martensite;
(4) the invention relates to a preparation method of high-carbon high-aluminum steel for drilling and lock making, which is characterized in that in the quenching process, the quenching temperature is controlled to be Accm-50～AccmThe temperature is controlled to promote dispersion and precipitation of a part of graphite particles in austenite, and the graphite particles are used as nucleation cores of the graphite particles in the subsequent tempering process to promote the growth of the graphite particles; in addition, placing the quenched steel billet into a muffle furnace at 650-710 ℃ for heat preservation for 2-5 h to inhibit the precipitation of cementite and accelerate the graphitization process of C;
(5) according to the preparation method of the high-carbon high-aluminum steel for drilling and locking, the tempering temperature is controlled to be 680-710 ℃, the tempering time is 2-3 hours, the tempering condition can promote uniform nucleation and rapid growth of tempered ferrite grains and graphite particles, the hardness of the steel is further reduced, and the chip removal and breaking capacity and the heat dissipation speed of a drill bit in the drilling process are improved.
Drawings
Figure 1 is a short tower + powdered drill cutting topography of example 2 of the present invention.
Fig. 2 is a powdered drill cutting morphology of comparative example 1.
FIG. 3 shows the metallographic structure of example 2 after heat preservation at 870 ℃ for 20min for quenching and tempering at 680 ℃ for 5 h.
FIG. 4 is a scanning electron microscope morphology of graphite particles in steel of example 2 after heat preservation at 870 ℃ for 20min for quenching and tempering at 680 ℃ for 5 h;
FIG. 5 is the result of the energy spectrum analysis at position 1 in FIG. 4;
FIG. 6 is the result of the spectral analysis at position 2 in FIG. 4;
FIG. 7 is the result of the spectral analysis at position 3 in FIG. 4;
fig. 8 is a continuous drilling physical diagram of the lock body material manufactured in the embodiment 2.
Detailed Description
For a further understanding of the invention, reference should be made to the following detailed description taken in conjunction with the accompanying drawings and examples.
Example 1
The high-carbon high-aluminum steel for drilling and lock making of the embodiment comprises the following chemical components in percentage by mass: c: 1.02%, Si: 0.35%, Mn: 0.54%, P: 0.015%, S: 0.026%, Bi: 0.058%, Al: 2.06%, N: 0.0056%, Ti: 0.025%, and the balance of Fe and inevitable impurities, while Si + Al is 2.41%.
A of the high-carbon high-aluminum steel of the exampleccmAt 875 ℃.
Example 2
The high-carbon high-aluminum steel for drilling and lock making of the embodiment comprises the following chemical components in percentage by mass: c: 1.15%, Si: 0.44%, Mn: 0.48%, P: 0.019%, S: 0.034%, Bi: 0.051%, Al: 2.17%, N: 0.0042%, Ti: 0.021%, the balance of Fe and inevitable impurities, and 2.61% of Si + Al.
A of the high-carbon high-aluminum steel of the exampleccm882 ℃.
Example 3
The high-carbon high-aluminum steel for drilling and lock making of the embodiment comprises the following chemical components in percentage by mass: c: 1.23%, Si: 0.49%, Mn: 0.39%, P: 0.028%, S: 0.028%, Bi: 0.046%, Al: 2.24%, N: 0.0035%, Ti: 0.024%, and the balance of Fe and inevitable impurities, while Si + Al is 2.73%.
A of the high-carbon high-aluminum steel of the exampleccmAt 911 ℃.
Example 4
The high-carbon high-aluminum steel for drilling and lock making of the embodiment comprises the following chemical components in percentage by mass: c: 1.31%, Si: 0.52%, Mn: 0.41%, P: 0.035%, S: 0.037%, Bi: 0.040%, Al: 2.36%, N: 0.0049%, Ti: 0.018%, the balance being Fe and inevitable impurities, while Si + Al is 2.88%.
A of the high-carbon high-aluminum steel of the exampleccmIt was 936 ℃.
Example 5
The high-carbon high-aluminum steel for drilling and lock making of the embodiment comprises the following chemical components in percentage by mass: c: 1.46%, Si: 0.56%, Mn: 0.32%, P: 0.022%, S: 0.023%, Bi: 0.034%, Al: 2.45%, N: 0.0033%, Ti: 0.013%, the balance of Fe and inevitable impurities, and 3.01% of Si + Al.
A of the high-carbon high-aluminum steel of the exampleccmIt was 987 ℃.
Comparative example 1
The HT200 gray cast iron comprises the following chemical components in percentage by mass: c: 3.32%, Si: 1.75%, Mn: 0.85%, P: 0.065%, S: 0.071% and the balance Fe and inevitable impurities.
The preparation method of the embodiment 1-5 comprises the following steps and technical parameters:
firstly, smelting the components in a vacuum induction furnace, and casting into a 500kg steel ingot;
step two, forging the cast steel ingot, heating the cast steel ingot in a muffle furnace at 1150 ℃, preserving heat for 1.5h, and forging the cast steel ingot into a billet of 100mm multiplied by 120mm multiplied by L;
step three, carrying out hot rolling on the steel billet, wherein the initial thickness of the initial rolling is 100mm, the initial rolling temperature of the steel billet is controlled to be 1150 ℃, and after the steel billet is soaked at 1150 ℃, carrying out 6-pass hot rolling, namely 100mm → 75mm → 58mm → 44mm → 35mm → 30mm → 26mm, the final rolling temperature is 900-930 ℃, and the final rolling thickness is 26 mm;
step four, putting the hot rolled steel billet into the corresponding AccmThe muffle furnace is heated for 20min and then is quickly put into water to be quenched to room temperature;
fifthly, putting the quenched steel billet into a muffle furnace at 680 ℃ for heat preservation for 5 hours for tempering; then cooling to room temperature;
and sixthly, removing an oxide layer on the surface of the billet by using a shot blasting machine, wherein the shot blasting amount is 120kg/min, the shot blasting time is 18min, and the initial shot blasting speed is 76m/s, so that the high-carbon high-aluminum steel is obtained.
Comparative example 1 a vacuum induction furnace smelting + die casting molding process was directly employed, followed by shot blasting.
And cutting the shot-blasted billet into lock body sizes of 40mm multiplied by 60mm multiplied by 25mm for continuous drilling. The method comprises the steps of carrying out continuous automatic drilling (the diameter of a drill bit is 15mm, the number of revolutions is 3000r/min) experiments by adopting a special drilling machine for the lock body, evaluating the drilling processability of the material through the hardness of the material, the density of graphite particles (the number of the graphite particles with the unit area of 1-10 mu m), the size of drill cuttings and the temperature of the head of the drill bit, measuring the Vickers hardness of the material by adopting a Vickers hardness tester, observing and counting the number of the graphite particles in steel by adopting a Leyca metallographic microscope and Adobe Photoshop software, and measuring the highest temperature of the head of the drill bit after the single drilling is finished by adopting an infrared thermal imager. Specific test results are shown in the following table. Fig. 1 and 2 are the short tower + powdered drill cuttings morphology of example 2 and the powdered drill cuttings morphology of comparative example 1, respectively.
TABLE 1 hardness and drill processability of examples of the present invention and comparative examples
| Test specimen | hardness/HV | Density of graphite particles/(piece/mm)2) | Drill chip shape | Temperature of drill bit head/° c |
| Example 1 | 108 | 24100 | Short tower + powder | 278 |
| Example 2 | 106 | 25500 | Short tower + powder | 274 |
| Example 3 | 108 | 26200 | Short tower + powder | 278 |
| Example 4 | 103 | 26900 | Short tower + powder | 272 |
| Example 5 | 104 | 27700 | Short tower + powder | 275 |
| Comparative example 1 | 105 | 0 (graphite in strip net distribution) | In the form of a powder | 262 |
As can be seen from the above table,the hardness of the lock body of embodiments 1 to 5 is reduced to 103 to 108HV, and the density of graphite particles of 1 to 10 μm in the steel reaches 24100 to 27700 particles/mm2The shape of the drilling cuttings is changed into a short tower shape and powder shape, the temperature of a drill bit is reduced to 272-278 ℃ in the drilling process, the drilling performance of the lock body is similar to that of HT200 grey cast iron in the comparative example 1, and the continuous drilling processing production requirement is met.
Furthermore, in 5 groups of examples, examples 2 and 3 are selected to carry out optimization experiments of different quenching and tempering processes, so that quantitative relations among quenching temperature, tempering time, material hardness, graphite particle density, drill chip shape and drill bit head temperature are obtained, and the drilling processability of the material is further improved. Table 2 shows the drilling processability of examples 2 and 3 under different quenching and tempering processes, specifically as follows:
table 2 drill processability for examples 2 and 3 under different quench and temper processes.
As can be seen from Table 2, the quenching temperature for obtaining the optimum drilling workability in example 2 was set to 840 ℃ to 870 ℃ (A)ccm-42～AccmThe tempering temperature is between 680 and 710 ℃, the tempering time is 2 to 3 hours, the corresponding product hardness is 103 to 107HV, and the graphite particle density is 24200 to 25300 particles/mm2The shape of the drill cuttings is short tower shape and powder shape, and the temperature of a drill bit in the drilling process is 273-277 ℃. Example 3 quenching temperature to obtain optimum drilling processability 870-900 deg.C (A)ccm-41～AccmThe tempering temperature is between 680 and 710 ℃, the tempering time is 2 to 3 hours, the corresponding product hardness is between 102 and 108HV, and the graphite particle density is 27100 to 28300 particles/mm2The shape of the drill cuttings is short tower shape and powder shape, and the temperature of a drill bit in the drilling process is 272-278 ℃. FIG. 3 shows the temperature of 870 ℃ for 20min in example 2A metallographic structure after quenching and tempering at 680 ℃ for 5 hours, and fig. 4-7 are scanning electron microscope morphology and energy spectrum analysis results of graphite particles in steel after heat preservation at 870 ℃ for 20min and quenching and tempering at 680 ℃ for 5 hours in example 2, and it can be seen that a large amount of graphite particles with a size of 1-10 μm and a shape of a nearly spherical shape exist in the steel, and fig. 8 is a continuous drilling object diagram of the lock body material prepared in example 2.
The present invention and its embodiments have been described above schematically, without limitation, and what is shown in the drawings is only one of the embodiments of the present invention, and the actual structure is not limited thereto. Therefore, if the person skilled in the art receives the teaching, without departing from the spirit of the invention, the person skilled in the art shall not inventively design the similar structural modes and embodiments to the technical solution, but shall fall within the scope of the invention.
Claims (7)
1. The utility model provides a high carbon high alumina steel for drilling system lock which characterized in that: the chemical components of the material by mass percent are: c: 1% -1.5%, Si: 0.3% -0.6%, Mn: 0.2% -0.6%, P: 0.01% -0.04%, S: 0.02% -0.04%, Bi: 0.03-0.06%, Al: 1.5% -2.5%, N: 0.003-0.006 percent of Ti: 0-0.03 percent, the balance of Fe and inevitable impurities, and Si + Al in the components is controlled to be more than or equal to 2.4 percent.
2. A preparation method of high-carbon high-aluminum steel for drilling and lock making is characterized by comprising the following steps:
step one, smelting by adopting a vacuum induction furnace, and casting into a steel ingot;
step two, forging the cast steel ingot to obtain a steel billet;
step three, carrying out hot rolling on the steel billet;
step four, rolling the steel billet in Accm-50～AccmKeeping the temperature in a muffle furnace at +50 ℃ for 20min, and quickly putting the muffle furnace into water to quench the muffle furnace to room temperature so as to promote complete martensite;
fifthly, putting the quenched steel billet into a muffle furnace at 650-720 ℃ for heat preservation for 2-5 h for tempering;
removing an oxide layer on the surface of the steel billet through shot blasting to obtain high-carbon high-aluminum steel;
the high-carbon high-aluminum steel comprises the following chemical components in percentage by mass: c: 1% -1.5%, Si: 0.3% -0.6%, Mn: 0.2% -0.6%, P: 0.01% -0.04%, S: 0.02% -0.04%, Bi: 0.03-0.06%, Al: 1.5% -2.5%, N: 0.003-0.006 percent of Ti: 0-0.03 percent, the balance of Fe and inevitable impurities, and Si + Al in the components is controlled to be more than or equal to 2.4 percent.
3. The method for preparing the high-carbon high-aluminum steel for drilling and locking according to claim 2, wherein the method comprises the following steps: the quenching temperature in the fourth step is Accm-50～Accm℃。
4. The method for preparing the high-carbon high-aluminum steel for drilling and locking according to claim 2, wherein the method comprises the following steps: in the fifth step, the tempering temperature is 680-710 ℃, and the tempering time is 2-3 h.
5. The method for preparing the high-carbon high-aluminum steel for drilling and locking according to claim 2, wherein the method comprises the following steps: in the second step, during forging, the heating temperature of the cast ingot is 1150 ℃, the heat preservation time is 1.5h, and the forged billet is 100mm multiplied by 120mm multiplied by L.
6. The method for preparing the high-carbon high-aluminum steel for drilling and locking according to claim 2, wherein the method comprises the following steps: in the third step, the initial rolling temperature of the billet is 1150 ℃, and the final rolling temperature is 900-930 ℃.
7. The method for preparing the high-carbon high-aluminum steel for drilling and locking according to claim 6, wherein the method comprises the following steps: in the third step, the initial thickness of the initial rolling of the billet is 100mm, and the rolling pass is 6; the final thickness was 26 mm.
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