CN111455149A - Isothermal spheroidizing annealing process for H13 steel - Google Patents
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- CN111455149A CN111455149A CN202010394621.8A CN202010394621A CN111455149A CN 111455149 A CN111455149 A CN 111455149A CN 202010394621 A CN202010394621 A CN 202010394621A CN 111455149 A CN111455149 A CN 111455149A
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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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
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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
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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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Abstract
The invention discloses an H13 steel isothermal spheroidizing annealing process, which comprises the following steps: axially upsetting and drawing out H13 steel blanks preheated to 1180 +/-15 ℃ and continuously preserving heat for at least 3 hours in a forging furnace for not less than 3 times, then radially upsetting, rounding and flattening for not less than 3 times, then air-cooling the forged H13 steel blanks to 470 +/-25 ℃, putting the H13 steel blanks into the furnace, heating to 620 +/-20 ℃ at a heating rate of 50 +/-25 ℃/H for quenching preheating and heat preservation for 1-1.5H, continuously heating to 870 +/-20 ℃ at a heating rate of 50 +/-25 ℃/H for preheating for 1-2H, entering and exiting for quenching for secondary preheating, enabling the fiber flow direction at the central part of the die to be distributed in the circumferential direction through a transverse fiber flow direction forging process, enabling the structure of the die to be uniform, enabling the carbide distribution of the carbide in the structure to be uniform, and simultaneously matching with two continuous quenching pretreatments after forging, eliminating reticular carbide, eliminate the defects of network carbide and the like in the original structure and reduce the annealing hardness.
Description
Technical Field
The invention relates to an annealing process, in particular to an isothermal spheroidizing annealing process for H13 steel, belonging to the technical field of die steel heat treatment processes.
Background
H13 steel is the most widely used hot work die steel at present, the steel is usually applied to the environments of rapid cooling, rapid heating, high temperature and high pressure, and the most main failure modes are thermal fatigue cracks, coarse cracks, plastic deformation, abrasion and the like, wherein the thermal fatigue cracks are the most main failure modes influencing the service life of the hot work die; it is generally believed that strength and temper stability are the most important factors affecting thermal fatigue resistance, while high impact toughness facilitates relaxation of local stresses, preventing crack propagation; strength and plasticity may have different effects on different stages of thermal fatigue; the initiation stage of the thermal fatigue crack is mainly controlled by strength, and the expansion stage is mainly controlled by toughness and plasticity, when thermal cracking occurs, the higher toughness of the steel can prevent the crack from expanding, and large cracks penetrating through the die are prevented from being formed; therefore, the high strength and the good toughness and plasticity contribute to the thermal fatigue resistance of the hot-working die material; the required strength can be obtained by a proper quenching and tempering process in production, but the improvement of the toughness needs to improve the quality of the steel, and for example, an isothermal spheroidizing annealing process for H13 steel is provided in the patent with the application number of CN 201710076783.5.
However, in the patent with the application number of CN201710076783.5, although improvement is provided in the H13 steel isothermal spheroidizing annealing process, such as carbide distribution uniformity in the structure, tissue refinement, elimination of network carbide and other defects in the original structure, and reduction of annealing hardness, the quenching effect is poor due to the defect of one-time preheating in the preheating process during quenching, and meanwhile, the H13 steel mold has uniform and dense structure and is insufficient in improvement of crystalline phase structure.
Disclosure of Invention
Aiming at the problems in the prior art, the invention provides an isothermal spheroidizing annealing process for H13 steel.
In order to solve the technical problem, the isothermal spheroidizing annealing process for the H13 steel provided by the invention comprises the following steps of:
s1: forging for multiple times, namely axially upsetting and drawing out H13 steel blanks preheated to 1180 +/-15 ℃ for at least 3 hours continuously and thermally insulating for at least 3 hours in a forging furnace for not less than 3 times, and then radially and sequentially upsetting, rounding and flattening for not less than 3 times to enable the circumferential direction of the die blanks to be the fiber flow direction;
s2: quenching, then air-cooling the forged H13 steel blank to 470 +/-25 ℃, loading into a furnace, raising the temperature to 620 +/-20 ℃ at the temperature rise speed of 50 +/-25 ℃/H, carrying out quenching preheating and heat preservation for 1-1.5H, continuing raising the temperature to 870 +/-20 ℃ at the temperature rise speed of 50 +/-25 ℃/H, carrying out preheating and heat preservation for 1-2H, carrying out secondary preheating in and out quenching, raising the temperature to 1000 +/-50 ℃ at the temperature rise speed of 50 +/-25 ℃/H, carrying out quenching on H13 steel, preserving the heat for 3-5H after the furnace burden is completely preserved, and then carrying out oil cooling or air cooling to less than or equal to 550 ℃ in the furnace;
s3: annealing and preheating treatment, namely, hot charging the quenched H13 blank material into a furnace, heating to 870 +/-20 ℃ at the heating rate of 50 +/-25 ℃/H, preserving the heat for 0.5 to 1H after the furnace charge is fully preserved, and discharging the furnace material in an oil cooling or air cooling manner to finish the pretreatment process;
s4: and (3) annealing treatment, namely, charging the H13 steel subjected to annealing pretreatment at the temperature of 350 +/-35 ℃, heating to 880 +/-10 ℃ at the heating rate of 50 +/-25 ℃/H, preserving heat for 4-6H, cooling to 760 +/-10 ℃ at the cooling rate of 17 +/-3 ℃/H, preserving heat for 8-12H, cooling to less than or equal to 500 ℃ at the cooling rate of 17 +/-3 ℃/H, air-cooling, and discharging to finish annealing.
Specifically, H13 steel rotates in multiple angles in the annealing furnace in the processes of preheating, heating, cooling and cooling H13 steel in the quenching and annealing pretreatment and annealing treatment processes.
Specifically, each process of axial upsetting, drawing, rounding and flattening of H13 steel blanks heats the H13 steel after operation.
Specifically, the H13 steel subjected to annealing pretreatment is placed in a furnace when the temperature is 350 ℃, the temperature is increased to 880 ℃ at the heating rate of 50 +/-25 ℃/H, the temperature is kept for 4-6H, the steel is cooled to 760 ℃ at the cooling rate of 17 +/-3 ℃/H, the temperature is kept for 8-12H, then the steel is cooled to be less than or equal to 500 ℃ at the cooling rate of 17 +/-3 ℃/H, and the steel is air-cooled and taken out of the furnace to finish annealing.
Specifically, the H13 steel subjected to annealing pretreatment is charged when the temperature is 360 ℃, the temperature is increased to 890 ℃ at the heating rate of 50 +/-25 ℃/H, the temperature is kept for 4-6H, the steel is cooled to 770 ℃ at the cooling rate of 17 +/-3 ℃/H, the temperature is kept for 8-12H, and then the steel is cooled to 500 ℃ or less at the cooling rate of 17 +/-3 ℃/H, and then the steel is air-cooled and taken out of the furnace to finish annealing.
Specifically, the H13 steel subjected to annealing pretreatment is placed in a furnace when the temperature is 350 ℃, the temperature is increased to 880 ℃ at the heating rate of 50 +/-25 ℃/H, the temperature is kept for 5H, the steel is cooled to 760 ℃ at the cooling rate of 17 +/-3 ℃/H, the steel is kept for 9H, and then the steel is cooled to be less than or equal to 500 ℃ at the cooling rate of 17 +/-3 ℃/H, and then the steel is air-cooled and taken out of the furnace to finish annealing.
Specifically, the H13 steel subjected to annealing pretreatment is placed in a furnace when the temperature is 350 ℃, the temperature is increased to 880 ℃ at the heating rate of 50 +/-25 ℃/H, the temperature is kept for 6H, the steel is cooled to 760 ℃ at the cooling rate of 17 +/-3 ℃/H, the temperature is kept for 11H, then the steel is cooled to be less than or equal to 500 ℃ at the cooling rate of 17 +/-3 ℃/H, and the steel is air-cooled and taken out of the furnace to finish annealing.
The invention has the beneficial effects that: the invention relates to an isothermal spheroidizing annealing process for H13 steel, which comprises the steps of axially upsetting and drawing an H13 steel blank which is preheated to 1180 +/-15 ℃ and continuously insulated for at least 3 hours for not less than 3 times in a forging furnace, then radially upsetting, rounding and flattening for not less than 3 times, enabling the circumferential direction of the die blank to be the fiber flow direction, then cooling the forged H13 steel blank to 470 +/-25 ℃, loading the forged H13 steel blank into the furnace, heating to 620 +/-20 ℃ at the heating rate of 50 +/-25 ℃/H for quenching preheating insulation for 1-1.5 hours, continuously heating to 870 +/-20 ℃ at the heating rate of 50 +/-25 ℃/H for preheating, keeping the temperature for 1-2 hours, entering and exiting for quenching for secondary preheating, enabling the fiber flow direction at the central part of the die to be distributed in the circumferential direction through a transverse fiber flow direction process, and enabling the structure of the die to be uniform and compact, carbide distribution uniformity in the structure, and simultaneously, after forging, the method is matched with two continuous quenching pretreatments, so that reticular carbide can be eliminated, the crystalline phase structure is improved, the defects of the reticular carbide and the like in the original structure are eliminated, the annealing hardness is reduced, in the quenching and annealing pretreatments, H13 steel rotates in multiple angles in the annealing furnace in the processes of preheating, heating and cooling H13 steel, the temperature change of the H13 steel is more stable, the heating and cooling are more uniform, and simultaneously, in the processes of axially upsetting, drawing, rounding and flattening H13 steel, each flow heats the operated H13 steel, the forging temperature is ensured to be 1180 +/-15 degrees every time, and the forging effect is better.
Drawings
The invention is further illustrated with reference to the following figures and examples.
Fig. 1 is a flow chart of a preferred embodiment of the isothermal spheroidizing annealing process for H13 steel according to the present invention.
Detailed Description
The technical solutions in the embodiments of the present invention will be clearly and completely described below with reference to the drawings in the embodiments of the present invention, and it is obvious that the described embodiments are only a part of the embodiments of the present invention, and not all of the embodiments. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
First embodiment
As shown in fig. 1, the isothermal spheroidizing annealing process for H13 steel provided by the present invention comprises the following steps:
s1: forging for multiple times, namely axially upsetting and drawing out H13 steel blanks preheated to 1180 +/-15 ℃ for at least 3 hours continuously and thermally insulating for at least 3 hours in a forging furnace for not less than 3 times, and then radially and sequentially upsetting, rounding and flattening for not less than 3 times to enable the circumferential direction of the die blanks to be the fiber flow direction;
s2: quenching, then air-cooling the forged H13 steel blank to 470 +/-25 ℃, loading into a furnace, raising the temperature to 620 +/-20 ℃ at the temperature rise speed of 50 +/-25 ℃/H, carrying out quenching preheating and heat preservation for 1-1.5H, continuing raising the temperature to 870 +/-20 ℃ at the temperature rise speed of 50 +/-25 ℃/H, carrying out preheating and heat preservation for 1-2H, carrying out secondary preheating in and out quenching, raising the temperature to 1000 +/-50 ℃ at the temperature rise speed of 50 +/-25 ℃/H, carrying out quenching on H13 steel, preserving the heat for 3-5H after the furnace burden is completely preserved, and then carrying out oil cooling or air cooling to less than or equal to 550 ℃ in the furnace;
s3: annealing and preheating treatment, namely, hot charging the quenched H13 blank material into a furnace, heating to 870 +/-20 ℃ at the heating rate of 50 +/-25 ℃/H, preserving the heat for 0.5 to 1H after the furnace charge is fully preserved, and discharging the furnace material in an oil cooling or air cooling manner to finish the pretreatment process;
s4: and (3) annealing treatment, namely, charging the H13 steel subjected to annealing pretreatment at the temperature of 350 +/-35 ℃, heating to 880 +/-10 ℃ at the heating rate of 50 +/-25 ℃/H, preserving heat for 4-6H, cooling to 760 +/-10 ℃ at the cooling rate of 17 +/-3 ℃/H, preserving heat for 8-12H, cooling to less than or equal to 500 ℃ at the cooling rate of 17 +/-3 ℃/H, air-cooling, and discharging to finish annealing.
Specifically, H13 steel rotates in multiple angles in the annealing furnace in the processes of preheating, heating, cooling and cooling H13 steel in the quenching and annealing pretreatment and annealing treatment processes.
Specifically, each process of axial upsetting, drawing, rounding and flattening of H13 steel blanks heats the H13 steel after operation.
Specifically, the H13 steel subjected to annealing pretreatment is placed in a furnace when the temperature is 350 ℃, the temperature is increased to 880 ℃ at the heating rate of 50 +/-25 ℃/H, the temperature is kept for 4-6H, the steel is cooled to 760 ℃ at the cooling rate of 17 +/-3 ℃/H, the temperature is kept for 8-12H, then the steel is cooled to be less than or equal to 500 ℃ at the cooling rate of 17 +/-3 ℃/H, and the steel is air-cooled and taken out of the furnace to finish annealing.
Second embodiment
Based on the isothermal spheroidizing annealing process for the H13 steel, which is provided by the first embodiment of the invention, the isothermal spheroidizing annealing process for the H13 steel is different in that the H13 steel subjected to annealing pretreatment is charged when the temperature is 360 ℃, the temperature is increased to 890 ℃ at the heating rate of 50 +/-25 ℃/H, the temperature is kept for 4-6H, the steel is cooled to 770 ℃ at the cooling rate of 17 +/-3 ℃/H, the steel is kept for 8-12H, and then the steel is cooled to 500 ℃ or less at the cooling rate of 17 +/-3 ℃/H, cooled and taken out of the furnace to finish annealing.
Third embodiment
Based on the isothermal spheroidizing annealing process for the H13 steel, which is provided by the second embodiment of the invention, the isothermal spheroidizing annealing process for the H13 steel, which is provided by the third embodiment of the invention, is different in that the H13 steel subjected to annealing pretreatment is placed in a furnace at 350 ℃, the temperature is increased to 880 ℃ at the temperature increasing speed of 50 +/-25 ℃/H, the temperature is kept for 5H, the steel is cooled to 760 ℃ at the cooling speed of 17 +/-3 ℃/H, and after the temperature is kept for 9 ℃, the steel is cooled to 500 ℃ or less at the cooling speed of 17 +/-3 ℃/H, and then the steel is air-cooled and taken out of the furnace to complete the annealing.
Fourth embodiment
Based on the isothermal spheroidizing annealing process for the H13 steel, which is provided by the third embodiment of the invention, the isothermal spheroidizing annealing process for the H13 steel, which is provided by the fourth embodiment of the invention, is different in that the H13 steel subjected to annealing pretreatment is placed in a furnace at 350 ℃, the temperature is increased to 880 ℃ at the temperature increasing speed of 50 +/-25 ℃/H, the temperature is kept for 6H, the steel is cooled to 760 ℃ at the cooling speed of 17 +/-3 ℃/H, the steel is kept for 11H, and then the steel is cooled to 500 ℃ or less at the cooling speed of 17 +/-3 ℃/H, and then the steel is air-cooled and taken out of the furnace to complete the annealing.
When the invention is used, firstly, H13 steel blank which is preheated to 1180 +/-15 ℃ and continuously insulated for at least 3 hours is axially upset and drawn for not less than 3 times in a forging furnace, then the H13 steel blank is radially upset, rounded and flattened for not less than 3 times, the circumferential direction of a die blank is in a fiber flow direction, then the forged H13 steel blank is air-cooled to 470 +/-25 ℃, the H13 steel blank is put into the furnace, the temperature is raised to 620 +/-20 ℃ at the temperature raising speed of 50 +/-25 ℃/H for quenching preheating and heat preservation for 1-1.5 hours, the temperature is raised to 870 +/-20 ℃ at the temperature raising speed of 50 +/-25 ℃/H for preheating and heat preservation for 1-2 hours, the H13 steel is quenched in and out for 1000 +/-50 ℃ at the temperature raising speed of 50 +/-25 ℃/H, the furnace charge is insulated for 3-5 hours after being thoroughly preserved, then the furnace is cooled to be not more than 550 ℃ for oil cooling or air cooling and is taken out of the furnace, then the quenched H13 blank material is hot-charged, the temperature is raised to 870 plus or minus 20 ℃ at the heating rate of 50 plus or minus 25 ℃/H, the furnace charge is kept warm for 0.5 to 1H after being fully preserved, oil cooling or air cooling discharging is carried out, the pretreatment process is completed, then the H13 steel which is annealed and pretreated is charged when the temperature is 350 plus or minus 35 ℃, the temperature is raised to 880 plus or minus 10 ℃ at the heating rate of 50 plus or minus 25 ℃/H, the temperature is kept for 4 to 6H, the H13 steel is cooled to 760 plus or minus 10 ℃ at the cooling rate of 17 plus or minus 3 ℃/H, the H13 steel is air cooled to be less than or equal to 500 ℃ after being kept warm for 8 to 12H, annealing is completed after being air cooled and discharged, the fiber flow direction of the central part of the die is distributed in the circumferential direction through the transverse fiber flow direction forging process, the structure of the die is relatively uniform and compact, the carbide distribution uniformity in the structure is matched with, the method has the advantages that the crystal phase structure is improved, the defects of network carbide and the like in the original structure are eliminated, the annealing hardness is reduced, the quenching and annealing pretreatment is performed, H13 steel is rotated at multiple angles in the annealing furnace in the processes of preheating, heating and cooling of H13 steel in the annealing treatment process, the temperature change of H13 steel is more stable, heating and cooling are more uniform, meanwhile, in the processes of axial upsetting, drawing, rounding and flattening of H13 steel blanks, each process heats the operated H13 steel, the forging temperature is 1180 +/-15 degrees every time, and the forging effect is better.
It will be evident to those skilled in the art that the invention is not limited to the details of the foregoing illustrative embodiments, and that the present invention may be embodied in other specific forms without departing from the spirit or essential attributes thereof. The present embodiments are therefore to be considered in all respects as illustrative and not restrictive, the scope of the invention being indicated by the appended claims rather than by the foregoing description, and all changes which come within the meaning and range of equivalency of the claims are therefore intended to be embraced therein. Any reference sign in a claim should not be construed as limiting the claim concerned.
Furthermore, it should be understood that although the present description refers to embodiments, not every embodiment may contain only a single embodiment, and such description is for clarity only, and those skilled in the art should integrate the description, and the embodiments may be combined as appropriate to form other embodiments understood by those skilled in the art.
Claims (7)
1. An isothermal spheroidizing annealing process for H13 steel, which is characterized by comprising the following steps:
s1: forging for multiple times, namely axially upsetting and drawing out H13 steel blanks preheated to 1180 +/-15 ℃ for at least 3 hours continuously and thermally insulating for at least 3 hours in a forging furnace for not less than 3 times, and then radially and sequentially upsetting, rounding and flattening for not less than 3 times to enable the circumferential direction of the die blanks to be the fiber flow direction;
s2: quenching, then air-cooling the forged H13 steel blank to 470 +/-25 ℃, loading into a furnace, raising the temperature to 620 +/-20 ℃ at the temperature rise speed of 50 +/-25 ℃/H, carrying out quenching preheating and heat preservation for 1-1.5H, continuing raising the temperature to 870 +/-20 ℃ at the temperature rise speed of 50 +/-25 ℃/H, carrying out preheating and heat preservation for 1-2H, carrying out secondary preheating in and out quenching, raising the temperature to 1000 +/-50 ℃ at the temperature rise speed of 50 +/-25 ℃/H, carrying out quenching on H13 steel, preserving the heat for 3-5H after the furnace burden is completely preserved, and then carrying out oil cooling or air cooling to less than or equal to 550 ℃ in the furnace;
s3: annealing and preheating treatment, namely, hot charging the quenched H13 blank material into a furnace, heating to 870 +/-20 ℃ at the heating rate of 50 +/-25 ℃/H, preserving the heat for 0.5 to 1H after the furnace charge is fully preserved, and discharging the furnace material in an oil cooling or air cooling manner to finish the pretreatment process;
s4: and (3) annealing treatment, namely, charging the H13 steel subjected to annealing pretreatment at the temperature of 350 +/-35 ℃, heating to 880 +/-10 ℃ at the heating rate of 50 +/-25 ℃/H, preserving heat for 4-6H, cooling to 760 +/-10 ℃ at the cooling rate of 17 +/-3 ℃/H, preserving heat for 8-12H, cooling to less than or equal to 500 ℃ at the cooling rate of 17 +/-3 ℃/H, air-cooling, and discharging to finish annealing.
2. The isothermal spheroidizing annealing process for H13 steel according to claim 1, characterized in that: in the quenching and annealing pretreatment, H13 steel rotates in multiple angles in the processes of preheating, heating, cooling and cooling H13 steel in the annealing treatment process.
3. The isothermal spheroidizing annealing process for H13 steel according to claim 1, characterized in that: in the processes of axial upsetting, drawing out, rounding and flattening of H13 steel blanks, each process heats the H13 steel after operation.
4. The isothermal spheroidizing annealing process for H13 steel according to claim 1, characterized in that: charging the annealed H13 steel at 350 ℃, heating to 880 ℃ at a heating rate of 50 +/-25 ℃/H, preserving heat for 4-6H, cooling to 760 ℃ at a cooling rate of 17 +/-3 ℃/H, preserving heat for 8-12H, cooling to 500 ℃ or less at a cooling rate of 17 +/-3 ℃/H, air-cooling, and discharging to finish annealing.
5. The isothermal spheroidizing annealing process for H13 steel according to claim 3, characterized in that: charging the annealed H13 steel at the temperature of 360 ℃, heating to 890 ℃ at the heating rate of 50 +/-25 ℃/H, preserving heat for 4-6H, cooling to 770 ℃ at the cooling rate of 17 +/-3 ℃/H, preserving heat for 8-12H, cooling to 500 ℃ or less at the cooling rate of 17 +/-3 ℃/H, air-cooling, and discharging to finish annealing.
6. The isothermal spheroidizing annealing process for H13 steel according to claim 5, characterized in that: charging the annealed H13 steel at 350 ℃, heating to 880 ℃ at a heating speed of 50 +/-25 ℃/H, preserving heat for 5H, cooling to 760 ℃ at a cooling speed of 17 +/-3 ℃/H, preserving heat for 9 ℃, cooling to 500 ℃ or less at a cooling speed of 17 +/-3 ℃/H, air-cooling, and discharging to finish annealing.
7. The isothermal spheroidizing annealing process for H13 steel according to claim 5, characterized in that: charging the annealed H13 steel at 350 ℃, heating to 880 ℃ at a heating rate of 50 +/-25 ℃/H, preserving heat for 6H, cooling to 760 ℃ at a cooling rate of 17 +/-3 ℃/H, preserving heat for 11H, cooling to 500 ℃ or less at a cooling rate of 17 +/-3 ℃/H, air-cooling, and discharging to finish annealing.
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| CN109280849A (en) * | 2018-10-26 | 2019-01-29 | 如皋市宏茂重型锻压有限公司 | A kind of high performance hot-work die steel and its manufacturing process |
| CN110193580A (en) * | 2019-06-11 | 2019-09-03 | 昆山众诚精密锻造有限公司 | A kind of H13 material forging mold technique |
| CN110484812A (en) * | 2019-04-29 | 2019-11-22 | 如皋市宏茂重型锻压有限公司 | A kind of high-performance hot stamping die steel and its manufacturing process |
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2020
- 2020-05-11 CN CN202010394621.8A patent/CN111455149A/en active Pending
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103173597A (en) * | 2013-02-28 | 2013-06-26 | 辽宁金钢重型锻造有限公司 | Method for improving optional performances of large H13 steel hot-extrusion mould |
| CN103333997A (en) * | 2013-07-02 | 2013-10-02 | 武汉钢铁(集团)公司 | Annealing heat treatment method of H13 die steel |
| CN106811580A (en) * | 2017-02-13 | 2017-06-09 | 钢铁研究总院 | A kind of annealing process of H13 hot die steels |
| CN109280849A (en) * | 2018-10-26 | 2019-01-29 | 如皋市宏茂重型锻压有限公司 | A kind of high performance hot-work die steel and its manufacturing process |
| CN110484812A (en) * | 2019-04-29 | 2019-11-22 | 如皋市宏茂重型锻压有限公司 | A kind of high-performance hot stamping die steel and its manufacturing process |
| CN110193580A (en) * | 2019-06-11 | 2019-09-03 | 昆山众诚精密锻造有限公司 | A kind of H13 material forging mold technique |
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Application publication date: 20200728 |