CN111733312B - Heat treatment process for improving comprehensive mechanical property of H13 steel - Google Patents
Heat treatment process for improving comprehensive mechanical property of H13 steel Download PDFInfo
- Publication number
- CN111733312B CN111733312B CN202010805082.2A CN202010805082A CN111733312B CN 111733312 B CN111733312 B CN 111733312B CN 202010805082 A CN202010805082 A CN 202010805082A CN 111733312 B CN111733312 B CN 111733312B
- Authority
- CN
- China
- Prior art keywords
- steel
- furnace
- heat treatment
- heating
- heat
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
- 238000010438 heat treatment Methods 0.000 title claims abstract description 137
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 117
- 239000010959 steel Substances 0.000 title claims abstract description 117
- 238000000034 method Methods 0.000 title claims abstract description 29
- 238000000137 annealing Methods 0.000 claims abstract description 19
- 238000010791 quenching Methods 0.000 claims abstract description 15
- 230000000171 quenching Effects 0.000 claims abstract description 15
- 238000005496 tempering Methods 0.000 claims abstract description 15
- 238000001816 cooling Methods 0.000 claims description 56
- 238000007599 discharging Methods 0.000 claims description 30
- 150000003839 salts Chemical class 0.000 claims description 8
- 239000011780 sodium chloride Substances 0.000 claims description 8
- 238000009776 industrial production Methods 0.000 abstract description 2
- 229910001563 bainite Inorganic materials 0.000 description 14
- 229910000734 martensite Inorganic materials 0.000 description 8
- 238000009864 tensile test Methods 0.000 description 6
- 229910001566 austenite Inorganic materials 0.000 description 5
- 229910000529 magnetic ferrite Inorganic materials 0.000 description 5
- 150000001247 metal acetylides Chemical class 0.000 description 5
- 230000001131 transforming Effects 0.000 description 5
- 229910000859 α-Fe Inorganic materials 0.000 description 5
- 239000011651 chromium Substances 0.000 description 4
- 239000012535 impurity Substances 0.000 description 3
- 238000004519 manufacturing process Methods 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- 229910001567 cementite Inorganic materials 0.000 description 2
- 239000006185 dispersion Substances 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 230000001788 irregular Effects 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- REDXJYDRNCIFBQ-UHFFFAOYSA-N aluminium(3+) Chemical class [Al+3] REDXJYDRNCIFBQ-UHFFFAOYSA-N 0.000 description 1
- OKTJSMMVPCPJKN-UHFFFAOYSA-N carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 125000004432 carbon atoms Chemical group C* 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000005272 metallurgy Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000006011 modification reaction Methods 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 239000010409 thin film Substances 0.000 description 1
Classifications
-
- 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
-
- 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
- C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
- C21D1/20—Isothermal quenching, e.g. bainitic hardening
-
- 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
- C21D1/28—Normalising
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/002—Heat treatment of ferrous alloys containing Cr
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
-
- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
Abstract
The invention discloses a heat treatment process for improving comprehensive mechanical property of H13 steel, belonging to the technical field of heat treatment processes and comprising five steps of spheroidizing annealing, normalizing, spheroidizing annealing, isothermal quenching and tempering. The process can improve the comprehensive mechanical property of the H13 steel, has simple process flow and easy control, and is beneficial to realizing industrial production.
Description
Technical Field
The invention relates to a heat treatment process, in particular to a heat treatment process for improving comprehensive mechanical properties of H13 steel.
Background
The H13 steel is under the mark of 4Cr5MoSiV1 in China. The H13 steel is a chromium-based hot-work die steel having excellent hardenability, and can be quench-hardened when cooled in air. The steel is widely used for industrial manufacture due to excellent hardenability and toughness, but the prior H13 steel subjected to conventional heat treatment has relatively poor comprehensive mechanical properties, and the Rockwell hardness is 52 HRC, AKUThe impact energy of the standard unnotched impact specimen is about 300J at 10J.
In order to improve the strength and the toughness of H13 steel, Chinese patent with application number 201910602981.X discloses high-toughness high-crack-resistance hot-work die steel and a manufacturing method thereof, wherein the Rockwell hardness is 45-48 HRC, the impact energy of a standard unnotched impact specimen is more than or equal to 350J, and the tensile strength is more than or equal to 1350 MPa. The Chinese patent with the application number of 201910216546.3 discloses H13 die steel and a production method thereof, and the impact energy of the standard unnotched impact specimen is more than or equal to 280J.
The prior art at least has the following technical problems:
the improved H13 steel is still relatively low in tensile strength and hardness, and relatively poor in toughness. In order to obtain H13 steel with more excellent mechanical properties, a series of adjustments and improvements on the alloy content and the treatment process of H13 steel are still needed.
Disclosure of Invention
The invention aims to provide a heat treatment process for improving comprehensive mechanical properties of H13 steel and improve comprehensive mechanical properties of H13 steel.
In order to solve the technical problems, the invention adopts the technical scheme that: a heat treatment process for improving comprehensive mechanical properties of H13 steel comprises the following steps:
(1) and spheroidizing annealing: putting H13 steel into a heating furnace, heating to 885-895 ℃ along with the furnace, preserving heat for 1-1.5H, cooling to 745-755 ℃ along with the furnace, preserving heat for 1-1.5H, cooling to 500 ℃ along with the furnace, and then discharging from the furnace for air cooling;
(2) normalizing: putting the H13 steel subjected to the heat treatment in the step (1) into a heating furnace, heating the H13 steel to 975-985 ℃ along with the furnace, preserving the heat for 1-1.5H, and then discharging the H13 steel out of the furnace and air cooling;
(3) and spheroidizing annealing: putting the H13 steel subjected to the heat treatment in the step (2) into a heating furnace, heating the H13 steel to 885-895 ℃ along with the furnace, preserving heat for 1-1.5H, cooling the H13 steel to 745-755 ℃ along with the furnace, preserving heat for 1-1.5H, cooling the H13 steel to 500 ℃ along with the furnace, and then discharging the H13 steel out of the furnace for air cooling;
(4) and isothermal quenching: putting the H13 steel subjected to the heat treatment in the step (3) into a heating furnace, heating to 1020-1040 ℃ along with the furnace, preserving heat for 20-30 min, then quickly cooling to 310-355 ℃ in a salt bath furnace, preserving heat for 3-5H, discharging and air cooling;
(5) and tempering: and (3) putting the H13 steel subjected to the heat treatment in the step (4) into a heating furnace, heating to 555-565 ℃, preserving heat for 1-1.5H, discharging from the furnace, air cooling, then putting into the heating furnace, heating to 575-585 ℃, preserving heat for 1-1.5H, discharging from the furnace, and air cooling.
The technical route of the method is as follows: the H13 steel is heated to 1030 ℃ for austenitization after the preliminary heat treatment of spheroidizing annealing, normalizing and spheroidizing annealing, then is put into a salt bath furnace with the temperature near the martensite start transformation point of austenite for isothermal bainite transformation, and then is air-cooled to room temperature to obtain a nano bainite structure.
The physical metallurgy principle of the method is as follows: heating the H13 steel blank to a temperature above Ac1 to dissolve irregular carbides in the original structure, and then cooling the H13 steel blank to a temperature below Ac1 to spheroidize the carbides. Heating the spheroidizing annealed H13 steel to a temperature above Ac3 in the subsequent normalizing process, preserving the heat, further dissolving irregular carbides into a matrix, changing the form and distribution of the carbides, performing air cooling to obtain a martensite structure, and then performing spheroidizing annealing once again to obtain fine and uniformly distributed spherical carbides in the H13 steel matrix structure. And then, after austenitizing and holding the H13 steel subjected to the preliminary heat treatment for a period of time, carrying out bainite transformation in the process of carrying out low-temperature (near the martensite start transformation point of austenite) isothermal quenching in a salt bath furnace, wherein thin-film austenite is distributed among bainite laths because Si element inhibits the precipitation of carbide in the isothermal transformation process, and the width of the bainite laths is reduced, namely nano bainite is formed. And the mechanical property of the nanometer bainite is very excellent, so that the comprehensive mechanical property of the H13 steel can be improved.
The pre-heat treatment of spheroidizing annealing, normalizing and spheroidizing annealing mainly has two functions: firstly, the hardness of the H13 steel can be reduced through the pretreatment, so that the H13 steel is convenient to cut and form and is prepared for subsequent heat treatment; secondly, H13 steel obtains spherical carbide with high spheroidization rate and dispersion distribution after the pretreatment. During the subsequent heat treatment, the spherical undissolved carbide can pin the grain boundary, prevent the growth of austenite grains and play the role of fine grain strengthening. Meanwhile, the spherical carbide distributed in a dispersion mode can passivate the crack tip, change the crack path, slow down the crack propagation and improve the toughness of the steel.
The nano bainite steel is more resistant to tempering than martensite steel, the strength and hardness of the nano bainite steel have smaller dependence on solid solution strengthening of carbon, and the thickness of bainite ferrite laths determines the overall strength. The traditional H13 steel adopts the heat treatment process of quenching and twice tempering to obtain a tempered martensite structure, in the tempering process, high-over-saturated carbon atoms are precipitated in the tempered martensite in the form of carburized particles, and the dislocation density of the martensite is also obviously reduced, so that the strength and hardness of the tempered martensite are sharply reduced along with the precipitation of cementite and the reduction of the dislocation density. The hardness of the nano bainite steel is not obviously reduced in a short-time tempering process, because the film-shaped residual austenite in the structure is decomposed into cementite and ferrite, carbide is precipitated at the boundary of bainite ferrite laths, and the precipitated carbide is pinned at the boundary to prevent the ferrite laths from coarsening and growing. As the strength and hardness of the nano bainite steel are mainly derived from the small thickness of bainite ferrite laths, the steel can resist the loss of hardness and strength, and therefore, the structure obtained by the H13 steel after being treated by the heat treatment process has better tempering performance and longer service life than the structure obtained by the heat treatment process of traditional quenching and twice tempering.
The invention has the beneficial effects that: 1. the comprehensive mechanical property of H13 steel is improved, the Charpy U-shaped notch impact energy of the H13 steel after isothermal quenching is 27-40J, the standard unnotched impact energy is more than or equal to 392J, the Rockwell hardness is 51-53.6 HRC, the tensile strength is 2002-2224 MPa, and the elongation is 10.8-16.2%; the standard Charpy U-shaped notch impact energy of the tempered H13 steel is 14-16J, the Rockwell hardness is 52.9-53.4 HRC, and the comprehensive mechanical properties of the heat-treated H13 steel are superior to those of the conventional heat-treated H13 steel; 2. the process flow is simple, easy to control and beneficial to realizing industrial production.
The present invention will be described in detail with reference to the accompanying drawings.
Drawings
FIG. 1 is a process diagram of heat treatment according to examples 1 to 6 of the present invention;
FIG. 2 is a tensile curve of H13 steel prepared in example 1;
FIG. 3 is a tensile curve of H13 steel prepared in example 2;
fig. 4 is a tensile curve of H13 steel prepared in example 3.
Detailed Description
The invention relates to a heat treatment process for improving comprehensive mechanical properties of H13 steel, which comprises the following steps.
(1) And spheroidizing annealing: putting H13 steel into a heating furnace, heating to 885-895 ℃ along with the furnace, preserving heat for 1-1.5H, cooling to 745-755 ℃ along with the furnace, preserving heat for 1-1.5H, cooling to 500 ℃ along with the furnace, and then discharging from the furnace for air cooling.
(2) Normalizing: and (2) putting the H13 steel subjected to the heat treatment in the step (1) into a heating furnace, heating to 975-985 ℃ along with the furnace, preserving heat for 1-1.5H, and then discharging from the furnace and air cooling.
(3) And spheroidizing annealing: and (3) putting the H13 steel subjected to the heat treatment in the step (2) into a heating furnace, heating to 885-895 ℃ along with the furnace, preserving heat for 1-1.5H, cooling to 745-755 ℃ along with the furnace, preserving heat for 1-1.5H, cooling to 500 ℃ along with the furnace, and then discharging from the furnace for air cooling.
(4) And isothermal quenching: and (4) putting the H13 steel subjected to the heat treatment in the step (3) into a heating furnace, heating to 1020-1040 ℃ along with the furnace, preserving heat for 20-30 min, then quickly cooling to 310-355 ℃ in a salt bath furnace, preserving heat for 3-5H, discharging from the furnace, and air cooling.
(5) And tempering: and (3) putting the H13 steel subjected to the heat treatment in the step (4) into a heating furnace, heating to 555-565 ℃, preserving heat for 1-1.5H, discharging from the furnace, air cooling, then putting into the heating furnace, heating to 575-585 ℃, preserving heat for 1-1.5H, discharging from the furnace, and air cooling.
The present invention will be described in detail with reference to specific examples.
Example 1, see figures 1 and 2, in this example.
Selecting H13 steel, wherein the chemical components and the mass percentage content are as follows: 0.450% of C, 5.100% of Cr, 1.240% of Mo, 0.860% of V, 0.800% of Si, 0.370% of Mn, 0.170% of Ni, 0.030% of S, 0.017% of P, and the balance of Fe and inevitable impurities.
(1) And spheroidizing annealing: putting H13 steel into a heating furnace, heating to 500-.
(2) Normalizing: and (2) putting the H13 steel subjected to the heat treatment in the step (1) into a heating furnace, heating to 600-650 ℃ at the speed of 200 ℃/H, preserving heat for 1H, heating to 980 ℃ at the speed of 200 ℃/H, preserving heat for 1.5H, and then discharging from the furnace for air cooling.
(3) Spheroidizing annealing: and (3) putting the H13 steel subjected to the heat treatment in the step (2) into a heating furnace, heating to 500-minus-one-year-temperature 600 ℃ at the speed of 200 ℃/H, preserving heat for 1H, heating to 890 ℃ at the speed of 200 ℃/H, preserving heat for 1.5H, cooling to 750 ℃ along with the furnace, preserving heat for 1.5H, taking the steel out of the furnace after the furnace is cooled to 500 ℃, and air-cooling.
(4) Isothermal quenching: and (3) putting the H13 steel (the size used by the invention is 11mm multiplied by 56 mm) after the heat treatment in the step (3) into a heating furnace, heating to 1030 ℃ and preserving the heat for 20min, then quickly cooling to 310 ℃ in a salt bath furnace and preserving the heat for 3H, and discharging and air cooling.
The specimens obtained in this example were subjected to a micro tensile test according to ASTM Metal tensile test method E8-09, and the stress-strain curves are shown in FIG. 2. The AKU of the sample is 40J, the standard unnotched impact energy is more than 500J, the Rockwell hardness is 51HRC, the tensile strength is 2002MPa, and the elongation is 16.2%.
The above results show that: the H13 steel treated by the method has better comprehensive mechanical property. Has the characteristics of high strength, high toughness and high plasticity.
Example 2, see figures 1 and 3, in this example.
Selecting H13 steel, wherein the chemical components and the mass percentage content are as follows: 0.450% of C, 5.100% of Cr, 1.240% of Mo, 0.860% of V, 0.800% of Si, 0.370% of Mn, 0.170% of Ni, 0.030% of S, 0.017% of P, and the balance of Fe and inevitable impurities.
(1) And spheroidizing annealing: putting H13 steel into a heating furnace, heating to 500-.
(2) Normalizing: and (2) putting the H13 steel subjected to the heat treatment in the step (1) into a heating furnace, heating to 600-650 ℃ at the speed of 200 ℃/H, preserving heat for 1H, heating to 980 ℃ at the speed of 200 ℃/H, preserving heat for 1.5H, and then discharging from the furnace for air cooling.
(3) Spheroidizing annealing: and (3) putting the H13 steel subjected to the heat treatment in the step (2) into a heating furnace, heating to 500-minus-one-year-temperature 600 ℃ at the speed of 200 ℃/H, preserving heat for 1H, heating to 890 ℃ at the speed of 200 ℃/H, preserving heat for 1.5H, cooling to 750 ℃ along with the furnace, preserving heat for 1.5H, taking the steel out of the furnace after the furnace is cooled to 500 ℃, and air-cooling.
(4) Isothermal quenching: and (3) putting the H13 steel (the size used by the invention is 11mm multiplied by 56 mm) after the heat treatment in the step (3) into a heating furnace, heating to 1030 ℃ and preserving the heat for 20min, then quickly cooling to 345 ℃ in a salt bath furnace and preserving the heat for 5H, discharging and air cooling.
The specimens obtained in this example were subjected to a micro tensile test according to ASTM Metal tensile test method E8-09, and the stress-strain curves are shown in FIG. 3. The AKU of the sample is 21J, the standard unnotched impact energy is 370J, the Rockwell hardness is 52.3HRC, the tensile strength is 2143MPa, and the elongation is 8.6%.
The above results show that: the H13 steel treated by the method has better comprehensive mechanical property. Has the characteristics of high strength, high toughness and high plasticity.
Example 3, see figures 1 and 4, in this example.
Selecting H13 steel, wherein the chemical components and the mass percentage content are as follows: 0.450% of C, 5.100% of Cr, 1.240% of Mo, 0.860% of V, 0.800% of Si, 0.370% of Mn, 0.170% of Ni, 0.030% of S, 0.017% of P, and the balance of Fe and inevitable impurities.
(1) And spheroidizing annealing: putting H13 steel into a heating furnace, heating to 500-.
(2) Normalizing: and (2) putting the H13 steel subjected to the heat treatment in the step (1) into a heating furnace, heating to 600-650 ℃ at the speed of 200 ℃/H, preserving heat for 1H, heating to 980 ℃ at the speed of 200 ℃/H, preserving heat for 1.5H, and then discharging from the furnace for air cooling.
(3) Spheroidizing annealing: and (3) putting the H13 steel subjected to the heat treatment in the step (2) into a heating furnace, heating to 500-minus-one-year-temperature 600 ℃ at the speed of 200 ℃/H, preserving heat for 1H, heating to 890 ℃ at the speed of 200 ℃/H, preserving heat for 1.5H, cooling to 750 ℃ along with the furnace, preserving heat for 1.5H, taking the steel out of the furnace after the furnace is cooled to 500 ℃, and air-cooling.
(4) Isothermal quenching: and (3) putting the H13 steel (the size used by the invention is 11mm multiplied by 56 mm) after the heat treatment in the step (3) into a heating furnace, heating to 1030 ℃ and preserving the heat for 20min, then quickly cooling to 355 ℃ in a salt bath furnace and preserving the heat for 3H, discharging and air cooling.
The specimens obtained in this example were subjected to a micro tensile test according to ASTM Metal tensile test method E8-09, and the stress-strain curves are shown in FIG. 4. The AKU of the sample is 27J, the standard unnotched impact energy is 392J, the Rockwell hardness is 53.6HRC, the tensile strength is 2224MPa, and the elongation is 10.8%.
The above results show that: the H13 steel treated by the method has better comprehensive mechanical property. Has the characteristics of high strength, high toughness and high plasticity.
Example 4, referring to fig. 1, differs from example 1 in that: the step (5) and tempering are added: and (3) putting the H13 steel subjected to the heat treatment in the step (4) into a heating furnace, heating to 560 ℃, preserving heat for 1H, discharging from the furnace, air cooling, then putting into the heating furnace, heating to 580 ℃, preserving heat for 1H, discharging from the furnace, and air cooling.
AKU of the sample obtained in this example was 14J, and the Rockwell hardness was 53.4 HRC.
The above results show that: the H13 steel treated by the method has better comprehensive mechanical property. Has the characteristics of high hardness and high toughness.
Example 5, referring to fig. 1, differs from example 2 in that: the step (5) and tempering are added: and (3) putting the H13 steel subjected to the heat treatment in the step (4) into a heating furnace, heating to 560 ℃, preserving heat for 1H, discharging from the furnace, air cooling, then putting into the heating furnace, heating to 580 ℃, preserving heat for 1H, discharging from the furnace, and air cooling.
AKU of the sample obtained in this example was 14J, and the Rockwell hardness was 53.2 HRC.
The above results show that: the H13 steel treated by the method has better comprehensive mechanical property. Has the characteristics of high hardness and high toughness.
Example 6, with reference to fig. 1, differs from example 3 in that: the step (5) and tempering are added: and (3) putting the H13 steel subjected to the heat treatment in the step (4) into a heating furnace, heating to 560 ℃, preserving heat for 1H, discharging from the furnace, air cooling, then putting into the heating furnace, heating to 580 ℃, preserving heat for 1H, discharging from the furnace, and air cooling.
AKU of the sample obtained in this example was 16J, and Rockwell hardness was 52.9 HRC.
The above results show that: the H13 steel treated by the method has better comprehensive mechanical property. Has the characteristics of high hardness and high toughness.
The mechanical properties of the examples are compared with those of conventional examples as shown in the following table.
As can be seen from the above table, the tensile strength, impact toughness and hardness of the H13 die steel treated by the heat treatment method of the invention are obviously superior to those of the H13 steel in the conventional example. The above results show that: the H13 steel treated by the method has better comprehensive mechanical property. Has the characteristics of high strength, high toughness and high plasticity.
Finally, it should be noted that: the above examples are only intended to illustrate the technical solution of the present invention and not to limit it; although the present invention has been described in detail with reference to preferred embodiments, those skilled in the art will understand that: modifications to the specific embodiments of the invention or equivalent substitutions for parts of the technical features may be made; without departing from the spirit of the present invention, it is intended to cover all aspects of the invention as defined by the appended claims.
Claims (7)
1. A heat treatment process for improving comprehensive mechanical properties of H13 steel is characterized by comprising the following steps:
(1) and spheroidizing annealing: putting H13 steel into a heating furnace, heating to 885-895 ℃ along with the furnace, preserving heat for 1-1.5H, cooling to 745-755 ℃ along with the furnace, preserving heat for 1-1.5H, cooling to 500 ℃ along with the furnace, and then discharging from the furnace for air cooling;
(2) normalizing: putting the H13 steel subjected to the heat treatment in the step (1) into a heating furnace, heating the H13 steel to 975-985 ℃ along with the furnace, preserving the heat for 1-1.5H, and then discharging the H13 steel out of the furnace and air cooling;
(3) and spheroidizing annealing: putting the H13 steel subjected to the heat treatment in the step (2) into a heating furnace, heating the H13 steel to 885-895 ℃ along with the furnace, preserving heat for 1-1.5H, cooling the H13 steel to 745-755 ℃ along with the furnace, preserving heat for 1-1.5H, cooling the H13 steel to 500 ℃ along with the furnace, and then discharging the H13 steel out of the furnace for air cooling;
(4) and isothermal quenching: putting the H13 steel subjected to the heat treatment in the step (3) into a heating furnace, heating to 1020-1040 ℃ along with the furnace, preserving heat for 20-30 min, then quickly cooling to 310-355 ℃ in a salt bath furnace, preserving heat for 3-5H, discharging and air cooling;
(5) and tempering: and (3) putting the H13 steel subjected to the heat treatment in the step (4) into a heating furnace, heating to 555-565 ℃, preserving heat for 1-1.5H, discharging from the furnace, air cooling, then putting into the heating furnace, heating to 575-585 ℃, preserving heat for 1-1.5H, discharging from the furnace, and air cooling.
2. The heat treatment process for improving the comprehensive mechanical property of the H13 steel according to claim 1, wherein the Charpy U-notch impact energy of the H13 steel after the isothermal quenching heat treatment in the step (4) is 27-40J.
3. The heat treatment process for improving the comprehensive mechanical property of the H13 steel according to claim 1, wherein the unnotched impact energy of the H13 steel after the isothermal quenching heat treatment in the step (4) is not less than 392J.
4. The heat treatment process for improving the comprehensive mechanical property of the H13 steel according to claim 1, wherein the Rockwell hardness of the H13 steel subjected to the isothermal quenching heat treatment in the step (4) is 51-53.6 HRC.
5. The heat treatment process for improving the comprehensive mechanical property of the H13 steel according to claim 1, wherein the tensile strength of the H13 steel after the isothermal quenching heat treatment in the step (4) is 2002-2224 MPa, and the elongation is 10.8-16.2%.
6. The heat treatment process for improving the comprehensive mechanical property of the H13 steel according to claim 1, wherein the Charpy U-notch impact energy of the H13 steel after the tempering heat treatment in the step (5) is 14-16J.
7. The heat treatment process for improving the comprehensive mechanical property of the H13 steel as claimed in claim 1, wherein the Rockwell hardness of the H13 steel after the tempering heat treatment in the step (5) is 52.9-53.4 HRC.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202010805082.2A CN111733312B (en) | 2020-08-12 | 2020-08-12 | Heat treatment process for improving comprehensive mechanical property of H13 steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202010805082.2A CN111733312B (en) | 2020-08-12 | 2020-08-12 | Heat treatment process for improving comprehensive mechanical property of H13 steel |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN111733312A CN111733312A (en) | 2020-10-02 |
| CN111733312B true CN111733312B (en) | 2021-06-22 |
Family
ID=72658330
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202010805082.2A Active CN111733312B (en) | 2020-08-12 | 2020-08-12 | Heat treatment process for improving comprehensive mechanical property of H13 steel |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN111733312B (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113718092A (en) * | 2021-08-06 | 2021-11-30 | 山西太钢不锈钢股份有限公司 | Homogenization treatment method of bamboo leaf-shaped annealed tissue |
| CN114703425B (en) * | 2022-04-07 | 2022-10-14 | 燕山大学 | Martensite and bainite dual-phase hot work die steel and preparation method thereof |
Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102534134A (en) * | 2012-01-06 | 2012-07-04 | 莱芜钢铁集团有限公司 | Bainite isothermal quenching thermal treatment process method for medium-carbon bearing steel |
| CN104046915A (en) * | 2014-04-28 | 2014-09-17 | 如皋市宏茂重型锻压有限公司 | Large-section high-performance hot work die steel for die casting and preparation technology thereof |
| CN106811580A (en) * | 2017-02-13 | 2017-06-09 | 钢铁研究总院 | A kind of annealing process of H13 hot die steels |
| CN107419076A (en) * | 2017-07-26 | 2017-12-01 | 繁昌县华特机械制造有限公司 | A kind of mould steel heat treatment process |
| CN107675077A (en) * | 2017-09-21 | 2018-02-09 | 燕山大学 | A kind of middle carbon nanometer bainite unimach, rod iron and preparation method thereof |
| CN108315658A (en) * | 2018-05-11 | 2018-07-24 | 浙江通特重型锻造有限公司 | A kind of steel alloy and its preparation process |
| CN108823381A (en) * | 2018-07-12 | 2018-11-16 | 河钢股份有限公司 | A kind of heat treatment process improving H13 hot-work die steel forging material structural homogenity |
-
2020
- 2020-08-12 CN CN202010805082.2A patent/CN111733312B/en active Active
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102534134A (en) * | 2012-01-06 | 2012-07-04 | 莱芜钢铁集团有限公司 | Bainite isothermal quenching thermal treatment process method for medium-carbon bearing steel |
| CN104046915A (en) * | 2014-04-28 | 2014-09-17 | 如皋市宏茂重型锻压有限公司 | Large-section high-performance hot work die steel for die casting and preparation technology thereof |
| CN106811580A (en) * | 2017-02-13 | 2017-06-09 | 钢铁研究总院 | A kind of annealing process of H13 hot die steels |
| CN107419076A (en) * | 2017-07-26 | 2017-12-01 | 繁昌县华特机械制造有限公司 | A kind of mould steel heat treatment process |
| CN107675077A (en) * | 2017-09-21 | 2018-02-09 | 燕山大学 | A kind of middle carbon nanometer bainite unimach, rod iron and preparation method thereof |
| CN108315658A (en) * | 2018-05-11 | 2018-07-24 | 浙江通特重型锻造有限公司 | A kind of steel alloy and its preparation process |
| CN108823381A (en) * | 2018-07-12 | 2018-11-16 | 河钢股份有限公司 | A kind of heat treatment process improving H13 hot-work die steel forging material structural homogenity |
Non-Patent Citations (4)
| Title |
|---|
| "热处理工艺对 H13 芯棒钢组织和力学性能的影响";胡平;《宝钢技术》;20181231(第5期);34-40页 * |
| "等温淬火对H13钢组织与性能的影响";马旭等;《轻工科技》;20170731(第7期);60-62页 * |
| 不同热处理对H13钢力学性能的影响;王宏奎;《机械工人》;19971115;24-26 * |
| 淬火工艺对H13钢韧性影响的研究;胡正前等;《武汉工业大学学报》;19961231;61-63 * |
Also Published As
| Publication number | Publication date |
|---|---|
| CN111733312A (en) | 2020-10-02 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN104032221B (en) | A kind of Nb-microalloying high-carbon-chromium bearing steel and hot rolling production method thereof | |
| CN111733312B (en) | Heat treatment process for improving comprehensive mechanical property of H13 steel | |
| US20090277539A1 (en) | Steel for Warm Working, Warm Working Method Using the Steel, and Steel Material and Steel Component Obtainable Therefrom | |
| CN105002425B (en) | Superhigh intensity superhigh tenacity oil casing pipe steel, petroleum casing pipe and its manufacture method | |
| CN105018854A (en) | High-heat-resistance hot work die steel and preparation method | |
| CN111254355B (en) | Bainite alloy steel heat and treatment process | |
| CN103088269B (en) | Pressure container steel having high toughness at -120 DEG C, and its production method | |
| CN107916364B (en) | Hot work die steel | |
| JP2011510175A (en) | High alloy cold die steel | |
| CN109487061B (en) | Heat treatment method of martensite precipitation hardening stainless steel 06Cr15Ni5Cu2Ti | |
| CN111893391A (en) | Nano bainite hot work die steel and preparation method thereof | |
| CN110205446A (en) | A kind of G520 martensitic precipitation heat treatment method | |
| CN113652605B (en) | High-toughness steel for automobile wheel, thin-wall automobile wheel and preparation method of steel | |
| CN109022710A (en) | The heat treatment method of nitrogenous plastic mould band steel | |
| CN106987765B (en) | Spring wire rod, steel wire and its manufacturing method of excellent corrosion resistance | |
| CN114058968A (en) | High-plasticity hot forming steel with oxidation resistance for automobile and hot forming process | |
| KR100957306B1 (en) | Forging steel using high frequency heat treatment and method for manufacturing the same | |
| CN110656293A (en) | Mo-containing high-hardness stainless steel, heat treatment process and formed member | |
| EP3155134A1 (en) | Method of heat treatment of bearing steel | |
| CN110484830A (en) | A kind of high nitrogen type hot die steel and preparation method thereof | |
| CN104988295A (en) | Heat treatment method for improving medium-carbon non-quenched and tempered steel connecting rod cracking performance | |
| CN109593921A (en) | The tufftride heat treatment method of mould steel | |
| CN113755765B (en) | Hydrogen-embrittlement-resistant ultrahigh-strength steel and manufacturing method thereof | |
| JP4265819B2 (en) | Cold forging steel with excellent nitriding properties and method for producing the same | |
| CN114086085B (en) | Forming process for controlling residual ferrite of 38Si7 elastic strip |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |