CN111334706A - High-strength bolt with uniform structure and grain refinement and manufacturing method thereof - Google Patents
High-strength bolt with uniform structure and grain refinement and manufacturing method thereof Download PDFInfo
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- CN111334706A CN111334706A CN201910237410.0A CN201910237410A CN111334706A CN 111334706 A CN111334706 A CN 111334706A CN 201910237410 A CN201910237410 A CN 201910237410A CN 111334706 A CN111334706 A CN 111334706A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
- C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
- C21D1/32—Soft annealing, e.g. spheroidising
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/0093—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for screws; for bolts
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
Abstract
The invention relates to a method for manufacturing a high-strength bolt with uniform structure and refined grains, which is mainly characterized in that a heat treatment process is added before thermal refining, so that the structure after thermal refining is uniform and the grains are refined, namely precipitated phases in the process flow are adjusted. After the precipitated phase adjustment treatment, fine second phase particles such as AlN, TiN, TiC, VC, NbC, V (C, N), Nb (C, N) and the like are fully dispersed and precipitated in a matrix structure, and the fine second phase particles play a role of pinning grain boundaries when being quenched and heated in subsequent thermal refining treatment, prevent the growth of austenite grains when being heated and play a role of refining grains; the precipitated phase adjustment treatment can also obtain fine pearlite and ferrite equilibrium state tissues, improve the austenite nucleation rate during subsequent quenching and heating and ensure uniform nucleation. And (4) carrying out thermal refining after the precipitated phase is adjusted, and finally obtaining the high-strength bolt with uniform structure and refined grains.
Description
Technical Field
The invention relates to a method for manufacturing a high-strength bolt with uniform structure and refined crystal grains, and also relates to bolt steel obtained by the method.
Background
The high-strength bolt is very commonly used on automobiles, and meanwhile, along with the requirement of light weight of the automobiles, the requirement of high-power miniaturization of engines and the continuous improvement of the performance of the whole automobiles, the performance requirement of the high-strength bolt is also continuously improved. When the stress on the bolt is increased and the increase of the section size is limited by the design structure, the improvement of the strength level, the fatigue performance, the delayed fracture performance and the like of the bolt is particularly important. In the traditional quenching and tempering process, crystal grains are easy to grow up after being kept at an austenitizing temperature for a long time, and the strength and the plastic toughness of the material are reduced by the coarse crystal grains. Meanwhile, the quenching, heating and heat-preserving temperature is low, so that insoluble V, Ti, Nb, N, Al and other micro-alloy elements are not dissolved in an austenite matrix, and only the alloy elements dissolved in the austenite during heating can effectively generate second-phase particles capable of pinning grain boundaries in the steel during cooling. The microalloy bolt steel is prepared by adding microalloy elements such as V, Ti, Nb, N, Al and the like on the basis of the original material, and the microalloy elements are precipitated in the steel in a stable second phase form, so that the microalloy bolt steel can play a role in inhibiting the growth of crystal grains. However, these second phase particles are dissolved (or incompletely dissolved), precipitated, and grown up in the hot working process if the process is improperly set, and the second phase particles are not dispersed and precipitated in a large amount, and the function of pinning the grain boundaries to prevent the grains from growing up is not fully exerted.
Disclosure of Invention
In order to refine grains of the bolt steel after quenching and tempering and improve the strength and the ductility and toughness of the bolt steel, micro alloy elements such as V, Ti, Nb, N, Al and the like are added into the bolt steel. In order to ensure that the second phase can fully analyze and pin the grain boundary to prevent the grain growth, the invention provides a precipitated phase adjusting method for refining the crystal grains after quenching and tempering.
A method for manufacturing high-strength bolt steel with uniform structure and refined crystal grains mainly comprises the following steps of raw material spheroidizing annealing, cold drawing, spheroidizing annealing, cold heading forming, thermal refining, machining, thread rolling and surface phosphating, wherein the raw material spheroidizing annealing, cold drawing, spheroidizing annealing, cold heading forming, thermal refining, machining, thread rolling, surface phosphating and the like are industrial conventional processes; a precipitated phase adjustment treatment process is arranged between cold heading forming and quenching and tempering treatment, and the precipitated phase adjustment treatment specifically comprises the following steps: s1 heating the workpiece formed by cold heading at 1150-1250 ℃ to austenitize, and preserving heat for at least 50min to ensure that the microalloy elements are fully dissolved in austenite; above 1150 ℃ mainly to allow the second phase particles to be fully dissolved into austenite, and not more than 1250 ℃ to prevent abnormal structure from being generated during cooling after the bolt steel is overheated.
S2, cooling to 800-900 ℃, and keeping the temperature for no more than 90min to ensure that second phase particles are fully fine, dispersed and separated out;
s3 is cooled to 650-700 ℃ again and is kept warm for at least 60min, so that austenite is transformed to a balanced structure to obtain pearlite and ferrite structures with fine lamellar spacing, austenite is transformed to the balanced structure to obtain pearlite and ferrite structures with fine lamellar spacing, and fine second-phase particles of TiC, VC, NbC and the like are precipitated and precipitated among phases;
s4, cooling to room temperature along with the furnace, and then carrying out thermal refining;
the quenching and tempering treatment is heating quenching and high-temperature tempering, and the fine and dispersed second-phase particles can play a role in pinning crystal boundaries during austenitizing and heating and can effectively hinder the growth of crystal grains; the fine pearlite and ferrite tissues in a balanced state can improve the austenite nucleation rate and make the austenite nucleation uniform during quenching and heating of quenching and tempering, thereby achieving the effects of grain refinement and tissue homogenization after quenching and tempering, and finally obtaining the high-strength bolt with uniform tissues and grain refinement.
The invention further defines the technical scheme as follows:
further, in S1, the microalloying elements are V, Ti, Nb, N, and Al.
Further, in S2 and S3, the second phase particles are specifically TiN, VC, NbC, Nb (C, N), V (C, N), AlN, and the particle diameters of these particles are different and can be as small as a nanometer.
Further, in S1, the diameter of the workpiece is smaller than 16mm, the heat preservation time is 50min, and the heat preservation time is longer than 50min if the size of the workpiece is larger than 16 mm.
Further, in S2, the second phase particles TiN, VC, NbC, Nb (C, N), V (C, N), AlN and the like are fully and uniformly dispersed and precipitated by cooling to 800-900 ℃ at a cooling speed of 0.5-3.0 ℃/S.
Further, in S3, rapidly cooling to 650-700 ℃ at a cooling speed of more than 2.0 ℃/S to transform austenite to a balanced structure, obtaining pearlite and ferrite structures with fine lamellar spacing, precipitating and precipitating fine second-phase particles such as TiC, VC, NbC and the like between phases, and then cooling along with the furnace.
The high-strength bolted steel with uniform structure and refined grains comprises the chemical components of, by mass, 0.38-0.45% of C and less than or equal to 0.25% of Si; mn: 0.30 to 0.60; p is less than or equal to 0.015, S is less than or equal to 0.010; cr: 0.90 to 1.10; mo: 0.50 to 0.60; v: 0.15 to 0.35; nb: 0.02 to 0.04; cu is less than or equal to 0.2; al is less than or equal to 0.030; ti is less than or equal to 0.01; n: 0.009-0.018, and the balance of Fe and inevitable impurities.
The steel is added with V, Ti, Nb, N, Al and other micro-alloy elements to precipitate in the form of stable second phase, such as AlN, TiN, TiC, VC, NbC, V (C, N), Nb (C, N) and the like, and the second phase particles do not dissolve at a high austenitizing temperature, thereby playing a role in inhibiting grain growth.
Tests show that the 42CrMoVNb bolt steel containing V, Ti, Nb, N and Al microalloy elements is subjected to the precipitated phase adjustment treatment at 1150 ℃, and the grains are fine after the quenching and tempering treatment (940 ℃ quenching and 590 ℃ tempering), and the equivalent diameter of the grains is about 20 mu m; adjusting the precipitated phase at 1250 ℃, and performing thermal refining (940 ℃ quenching and 590 ℃ tempering) to obtain fine crystal grains with the equivalent diameter of about 15 um; the grain size of the crystal grain which is not subjected to precipitated phase adjustment and is directly subjected to thermal refining is about 35 um. The precipitated phase adjusting method can effectively promote a large amount of dispersed precipitation of second phase particles, prevent the crystal grains from growing in the subsequent quenching and tempering process, and refine the quenched and tempered crystal grains.
Drawings
FIG. 1(a) test (2) grain diagram;
FIG. 1(b) test (4) grain diagram;
FIG. 1(c) test (5) grain diagram.
Detailed Description
Example 1
A method for manufacturing a high-strength bolt with uniform structure and refined crystal grains mainly comprises the steps of raw material spheroidizing annealing, cold drawing, spheroidizing annealing, cold heading forming, precipitated phase adjusting treatment, thermal refining, machining, thread rolling, surface phosphating and the like. The precipitated phase adjustment treatment mainly comprises: heating to 1150 deg.C, maintaining for 50min, cooling to 820 deg.C at a cooling rate of 0.5 deg.C/s, maintaining for 30min, rapidly cooling to 650 deg.C at a cooling rate of more than 2.0 deg.C/s, maintaining for more than 60min, and furnace cooling to room temperature. And then, carrying out 940 ℃ heat preservation for 40min (quenching) and 590 ℃ heat preservation for 60min (high-temperature tempering) on the material, namely carrying out thermal refining treatment, wherein the equivalent diameter of the crystal grains after thermal refining treatment is about 24um, and the crystal grains are fine.
Example 2
A method for manufacturing a high-strength bolt with uniform structure and refined crystal grains mainly comprises the steps of raw material spheroidizing annealing, cold drawing, spheroidizing annealing, cold heading forming, precipitated phase adjusting treatment, thermal refining, machining, thread rolling, surface phosphating and the like. The precipitated phase adjustment treatment mainly comprises: heating to 1150 deg.C, maintaining for 50min, cooling to 850 deg.C at a cooling rate of 2.5 deg.C/s, maintaining for 40min, rapidly cooling to 650 deg.C at a cooling rate of more than 2.0 deg.C/s, maintaining for more than 60min, and furnace cooling to room temperature. And then, carrying out 940 ℃ heat preservation for 40min (quenching) and 595 ℃ heat preservation for 60min (high-temperature tempering) on the material, namely carrying out thermal refining, wherein the equivalent diameter of the crystal grains after thermal refining is about 22um, and the crystal grains are fine.
Example 3
A method for manufacturing a high-strength bolt with uniform structure and refined crystal grains mainly comprises the steps of raw material spheroidizing annealing, cold drawing, spheroidizing annealing, cold heading forming, precipitated phase adjusting treatment, thermal refining, machining, thread rolling, surface phosphating and the like. The precipitated phase adjustment treatment mainly comprises: heating to 1180 deg.C, maintaining for 50min, cooling to 880 deg.C at a cooling rate of 2.5 deg.C/s, maintaining for 50min, rapidly cooling to 650 deg.C at a cooling rate of more than 2.0 deg.C/s, maintaining for more than 60min, and furnace cooling to room temperature. And then, carrying out 940 ℃ heat preservation for 40min (quenching) and 600 ℃ heat preservation for 60min (high-temperature tempering) on the material, namely carrying out thermal refining treatment, wherein the equivalent diameter of the crystal grains after thermal refining treatment is about 20 mu m, and the crystal grains are fine.
Example 4
A method for manufacturing a high-strength bolt with uniform structure and refined crystal grains mainly comprises the steps of raw material spheroidizing annealing, cold drawing, spheroidizing annealing, cold heading forming, precipitated phase adjusting treatment, thermal refining, machining, thread rolling, surface phosphating and the like. The precipitated phase adjustment treatment mainly comprises: heating to 1200 deg.C, maintaining the temperature for 50min, cooling to 900 deg.C at a cooling rate of 2.5 deg.C/s, maintaining the temperature for 40min, rapidly cooling to 650 deg.C at a cooling rate of more than 2.0 deg.C/s, maintaining the temperature for more than 60min, and furnace cooling to room temperature. And then, carrying out 940 ℃ heat preservation for 45min (quenching) and 595 ℃ heat preservation for 90min (high-temperature tempering) on the material, namely carrying out thermal refining, wherein the equivalent diameter of the crystal grains after thermal refining is about 19 mu m, and the crystal grains are fine.
Example 5
A method for manufacturing a high-strength bolt with uniform structure and refined crystal grains mainly comprises the steps of raw material spheroidizing annealing, cold drawing, spheroidizing annealing, cold heading forming, precipitated phase adjusting treatment, thermal refining, machining, thread rolling, surface phosphating and the like. The precipitated phase adjustment treatment mainly comprises: heating to 1250 deg.C, keeping the temperature for 50min, cooling to 900 deg.C at a cooling rate of 2.5 deg.C/s, keeping the temperature for 60min, rapidly cooling to 650 deg.C at a cooling rate of more than 2.0 deg.C/s, keeping the temperature for more than 60min, and cooling to room temperature with the furnace. And then, carrying out 940 ℃ heat preservation for 45min (quenching) and 595 ℃ heat preservation for 90min (high-temperature tempering) on the material, namely carrying out thermal refining, wherein the equivalent diameter of the crystal grains after thermal refining is about 15 mu m, and the crystal grains are fine.
The gear steel added with V, Ti, Nb, N and Al micro-alloy elements is selected as a raw material, and the raw material is forged and then subjected to precipitated phase adjustment treatment. The test shows that: in the test (1), the temperature for heating austenitizing by precipitated phase adjustment treatment is 900 ℃, the temperature is kept for 40min when the precipitated phase is cooled to 880 ℃ at the cooling rate of 1 ℃/s after the temperature is kept for 60min, then the precipitated phase is quickly cooled to 560 ℃ at the cooling rate of 3.5 ℃/s, the temperature is kept for 60min, and then the temperature is kept for 60min in a subsequent furnace. And then carrying out carburizing at 960 ℃ for 5h, and detecting that the equivalent diameter of the carburized crystal grains is 33-35 um. The temperature for heating austenitizing in the precipitated phase adjustment treatment in the test (2) is 1000 ℃, the temperature is kept for 40min when the precipitated phase is cooled to 880 ℃ at the cooling speed of 1 ℃/s after the temperature is kept for 60min, then the precipitated phase is quickly cooled to 560 ℃ at the cooling speed of 3.5 ℃/s, the temperature is kept for 60min, and then the temperature is kept for 60min in a subsequent furnace. And then carrying out carburizing at 960 ℃ for 5h, and detecting that the equivalent diameter of the carburized crystal grains is 30-33 um, wherein the picture of the crystal grains is shown in figure 1 (a). The temperature for heating austenitizing in the precipitated phase adjustment treatment in the test (3) is 1100 ℃, the temperature is kept for 40min when the precipitated phase is cooled to 880 ℃ at the cooling speed of 1 ℃/s after the temperature is kept for 60min, then the precipitated phase is quickly cooled to 560 ℃ at the cooling speed of 3.5 ℃/s, the temperature is kept for 60min, and then the furnace is cooled to the room temperature. And then carrying out carburizing at 960 ℃ for 5h, and detecting that the equivalent diameter of the carburized crystal grains is 20-23 um. The temperature for heating austenitizing in the precipitated phase adjustment treatment in the test (4) is 1200 ℃, the temperature is kept for 40min when the precipitated phase is cooled to 880 ℃ at the cooling speed of 1 ℃/s after the temperature is kept for 60min, then the precipitated phase is quickly cooled to 560 ℃ at the cooling speed of 3.5 ℃/s, the temperature is kept for 60min, and then the furnace is cooled to the room temperature. And then carrying out carburizing at 960 ℃ for 5h, and detecting that the equivalent diameter of the carburized crystal grains is 16-20 um, wherein the picture of the crystal grains is shown in figure 1 (b). In the test (5), the material which is not subjected to precipitated phase adjustment is subjected to carburization at 960 ℃ for 5 hours, the equivalent diameter of grains after carburization is detected to be 40-42 um, and the picture of the grains is shown in fig. 1 (c). Therefore, the precipitated phase adjustment treatment of the invention can effectively control the mass dispersion precipitation of the second phase particles, prevent the grain growth during carburization and refine the carburized grains.
The foregoing shows and describes the general principles, essential features, and advantages of the invention. It will be understood by those skilled in the art that the present invention is not limited to the embodiments described above, which are described in the specification and illustrated only to illustrate the principle of the present invention, but that various changes and modifications may be made therein without departing from the spirit and scope of the present invention, which fall within the scope of the invention as claimed. Therefore, the protection scope of the present invention shall be subject to the protection scope defined by the claims.
Claims (7)
1. A method for manufacturing a high-strength bolt with uniform structure and refined crystal grains mainly comprises the following steps of raw material spheroidizing annealing, cold drawing, spheroidizing annealing, cold heading forming, precipitated phase adjusting treatment, thermal refining treatment, machining, thread rolling and surface phosphating treatment, and is characterized in that the precipitated phase adjusting treatment step is arranged between the cold heading forming step and the thermal refining treatment step, and the precipitated phase adjusting treatment specifically comprises the following steps: s1 heating the workpiece formed by cold heading at 1150-1250 ℃ to austenitize, and preserving heat for at least 50min to ensure that the microalloy elements are fully dissolved in austenite;
s2, cooling to 800-900 ℃, and keeping the temperature for no more than 90min to ensure that second phase particles are fully fine, dispersed and separated out;
s3 is cooled to 650-700 ℃ again and is kept warm for at least 60min, so that austenite is transformed to a balanced structure to obtain pearlite and ferrite structures with fine interlamellar spacing, and fine second phase particles are precipitated and precipitated among phases;
s4, cooling to room temperature along with the furnace, and then carrying out thermal refining;
the quenching and tempering treatment comprises heating quenching and high-temperature tempering, and finally the high-strength bolt with uniform structure and refined grains is obtained.
2. The method for producing a uniform-structure, grain-refined, high-strength bolt according to claim 1, wherein in S1, the microalloying elements are V, Ti, Nb, N, and Al.
3. The method of claim 1, wherein the second phase particles of S2 and S3 are TiN, VC, NbC, Nb (C, N), V (C, N), AlN.
4. The method of claim 1, wherein in step S1, the diameter of the workpiece is less than 16mm, the temperature is maintained for 50min, and the temperature is maintained for more than 50min if the workpiece size is greater than 16 mm.
5. The method for manufacturing a uniform-structure, grain-refined, high-strength bolt as claimed in claim 1, wherein in S2, the bolt is cooled to 800-900 ℃ at a cooling rate of 0.5-3.0 ℃/S.
6. The method for manufacturing a uniform-structure, grain-refined, high-strength bolt according to claim 1, wherein in S3, the bolt is rapidly cooled to 650-700 ℃ at a cooling rate of more than 2.0 ℃/S.
7. The high-strength bolt with uniform structure and refined crystal grains is characterized in that the bolt steel comprises the following chemical components in percentage by mass, 0.38-0.45% of C, and less than or equal to 0.25% of Si; mn: 0.30 to 0.60; p is less than or equal to 0.015, S is less than or equal to 0.010; cr: 0.90 to 1.10; mo: 0.50 to 0.60; v: 0.15 to 0.35; nb: 0.02 to 0.04; cu is less than or equal to 0.2; al is less than or equal to 0.030; ti is less than or equal to 0.01; n: 0.009-0.018, and the balance of Fe and inevitable impurities.
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN115074605A (en) * | 2022-08-22 | 2022-09-20 | 中特泰来模具技术有限公司 | Hot work die steel and preparation method thereof |
| CN115074605B (en) * | 2022-08-22 | 2022-11-22 | 中特泰来模具技术有限公司 | Hot work die steel and preparation method thereof |
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