CN115595408A - Heat treatment process of spheroidized annealed high-hardenability high-carbon chromium steel - Google Patents
Heat treatment process of spheroidized annealed high-hardenability high-carbon chromium steel Download PDFInfo
- Publication number
- CN115595408A CN115595408A CN202211324462.XA CN202211324462A CN115595408A CN 115595408 A CN115595408 A CN 115595408A CN 202211324462 A CN202211324462 A CN 202211324462A CN 115595408 A CN115595408 A CN 115595408A
- Authority
- CN
- China
- Prior art keywords
- heat treatment
- product
- carbon chromium
- chromium steel
- treatment process
- 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.)
- Pending
Links
Images
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
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- 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
- C21D1/34—Methods of heating
- C21D1/44—Methods of heating in heat-treatment baths
-
- 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
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- 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
- 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
-
- 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
-
- 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
-
- 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
- C21D2211/001—Austenite
-
- 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
-
- 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
- C21D2211/004—Dispersions; Precipitations
-
- 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
- C21D2211/008—Martensite
Abstract
The invention relates to a heat treatment process of spheroidizing annealed high-hardenability high-carbon chromium steel, wherein a microstructure of the high-carbon chromium steel before heat treatment is a spheroidizing annealed structure, and granular carbides are distributed on a ferrite matrix, and the heat treatment process comprises the following steps: heating the high carbon chromium steel product to Ac cm Keeping the temperature in the temperature range of 30-50 ℃, wherein the heat preservation time is 1.5 min/mm-3.0 min/mm ﹡ d, and d is the diameter of the round steel or the longest straight line distance on the section of the product and is unit mm; step two: quenching the product after heat preservation in an alkali bath at 190-210 ℃, and quenching the product in the alkali bath to the bath temperature; step three: and (3) preserving the heat of the product treated in the step (II) in an alkaline bath for 25-35 min/mm ﹡ d, wherein d is the diameter of the round steel or the longest straight line distance on the section of the product, and is unit mm, and then cooling the product away from the bath in air. The heat treatment process realizes the obvious improvement of the strength, the toughness and the hardness of the spheroidized annealed high-carbon chromium steel.
Description
Technical Field
The invention relates to heat treatment of metal materials, in particular to a heat treatment process of spheroidized annealed steel.
Background
The high-carbon chromium steel is the most common steel for manufacturing wear-resistant parts, and the high-carbon chromium steel which is brought into the standard in China comprises GCr4, GCr15SiMn and the like. The selection of suitable materials for manufacturing mechanical parts has a great influence on the use performance and the service life of the mechanical parts, and the use performance of the materials is determined by the raw materials and the heat treatment process of the raw materials. For high-precision wear-resistant parts, not only high strength, high wear resistance, high elastic limit, suitable hardness, but also certain impact toughness and good dimensional stability are required.
For parts with smaller specifications (generally referring to diameters), GCr15 or GCr15SiMn steel with lower hardenability is often selected for production, and heat treatment processes capable of fully exerting the strength and toughness of the series of materials are developed at home and abroad. For parts with larger diameters, the steel grade is difficult to meet the hardenability requirement, so that the toughness of the parts after heat treatment is insufficient, the difference between the mechanical properties of the surface and the core is large, and the comprehensive performance requirement of a high-precision wear-resistant part is difficult to meet. Therefore, it is necessary to develop a material having higher hardenability by redesigning the conventional high carbon chromium steel. And the development of new products needs to be matched with a corresponding heat treatment process, and generally, the wear-resistant steel needs to realize the regulation and control of the structure performance through spheroidizing annealing and quenching and tempering processes. The material softening and the transformation of the flaky pearlite phase into the granular carbide structure can be realized through spheroidizing annealing, the regulation and control of the grain size and the spacing of the carbide are realized, and the structure and the performance of the final product of the part need to be regulated and controlled through a subsequent quenching process, so that the matching of the strengthening phase martensite, the bainite, the carbide and the toughness phase residual austenite in the microstructure of the spheroidizing annealed wear-resistant steel after quenching heat treatment is researched, the complex phase structure design is realized, and the comprehensive improvement of the toughness of the material can be realized.
Disclosure of Invention
The invention aims to provide a heat treatment process for spheroidizing annealed high-carbon chromium steel aiming at the prior art so as to obtain a specific complex phase structure and obviously improve the mechanical properties of steel, particularly the strength, the toughness and the hardness.
The technical scheme adopted by the invention for solving the problems is as follows: a heat treatment process of spheroidized annealed high-hardenability high-carbon chromium steel, wherein a microstructure before heat treatment of the high-carbon chromium steel is a spheroidized annealed structure, and granular carbides are distributed on a ferrite matrix, and the process comprises the following steps: heating the high carbon chromium steel product to A cm Keeping the temperature of the temperature range from 30 ℃ to 50 ℃ (870 ℃ to 890 ℃), wherein the temperature keeping time is 1.5min/mm to 3.0min/mm ﹡ d, and d is the diameter of the round steel or the longest straight line distance on the section of the product and is unit mm; step two: quenching the product after heat preservation in an alkali bath at 190-210 ℃, and quenching the product in the alkali bath to the bath temperature; step three: and (3) preserving the heat of the product treated in the step (II) in an alkaline bath for 25-35 min/mm ﹡ d, wherein d is the diameter of the round steel or the longest straight line distance on the section of the product, and is unit mm, and then cooling the product away from the bath in air.
Preferably, before the heat treatment, the spheroidized annealed structure has an average diameter of the particulate carbides of 0.40 to 0.7 μm and a spacing between the particulate carbides of 0.10 to 0.20. Mu.m.
Preferably, the weight percentage of the elements of the high-carbon chromium steel satisfies C:0.95 to 1.05%, si:0.20 to 0.30%, mn:0.60 to 0.80%, cr:1.65 to 1.75%, mo:0.40 to 0.50 percent, and the balance of Fe and inevitable impurities. Different from the traditional high-carbon chromium steel, the design of the element composition meets the requirement of high hardenability, and the hardenability depth is increased by 8mm. After spheroidizing annealing, the microstructure of the component material is a fine and uniform spheroidizing annealing structure, namely granular carbides are distributed on a ferrite matrix, the size of the granular carbides is smaller, the average diameter is about 0.40 mu m, the spacing between the granular carbides is 0.10-0.20 mu m, and the hardness is 221HBW.
Preferably, in step one, the heating temperature of the product is Ac cm Above 35 deg.C, (880 deg.C).
Preferably, in the second step, the temperature of the alkali bath is 200 ℃.
Preferably, in step two, the isothermal medium of said alkaline bath is NaOH + KOH, further the isothermal medium of said alkaline bath is 37wt% NaOH +63wt% KOH, to suit the quenching cooling capacity required.
Preferably, the product is heat treated to obtain a structure with a hardening phase martensite based on the lower bainite, and residual austenite + particulate carbides, the entire structure being dominated by the lower bainite, the hardening phase martensite being present in minor amounts as necessary.
In the technical scheme, the heating temperature in the first step is 870-890 ℃. The austenitizing heating temperature is determined primarily by the critical point of transformation of the steel, usually to Ac cm Ac of the high-carbon chromium steel according to the chemical components at the temperature of between 30 and 50 DEG C cm At about 845 ℃. The heating temperature is too low, austenitization is insufficient, particle carbides (larger than the particle carbides after heat treatment) in the original spheroidizing annealing structure are less dissolved, the particle carbides are easy to become crack initiation points in the service process, and the toughness of the heat-treated material is reduced; however, if the heating temperature is too high, the carbide dissolves in the matrix more, which results in an increase in the carbon content of the matrix, and if the carbon content in the matrix is too high, the toughness after the quenching heat treatment is also deteriorated (which is a drawback of the high carbon material), and further, if the heating temperature is too high, austenite grains are coarsened, which further deteriorates the toughness. Therefore, during the heat treatment, the control of the heating temperature is very critical, and Ac is the most preferable cm Above 35 deg.C, i.e. 880 deg.C.
In the technical scheme, the heat preservation time of the first step is 1.5 min/mm-3.0 min/mm. Too short heat preservation time, insufficient austenitization and too long result in excessive dissolution of particle carbides, excessive carbon content in a matrix, reduced toughness of the matrix, coarsening of austenite grains and energy waste, which are also not beneficial to obtaining target tissues and performances.
In the technical scheme, the isothermal temperature in the second step is 190-210 ℃, so that good toughness is obtained, the structure needs to be regulated and controlled to be a structure with a small amount of hardening phase martensite on the basis of lower bainite, and if the isothermal temperature is too high, pearlite or an upper bainite structure is easily formed, which is not favorable for forming lower bainite and martensite; and if the isothermal temperature is too low, more martensite structures are easily formed, the formation of lower bainite is not favorable, and the material is brittle.
In the technical scheme, the heat preservation time of the third step is particularly critical, the final structure is obviously influenced, in order to ensure that a good martensite, lower bainite, residual austenite and granular carbide complex phase structure is obtained after isothermal quenching, the heat preservation time needs to be regulated and controlled, the bainite transformation is between the diffusion transformation of a high-temperature region and the shear of a low-temperature region, the formation of bainite needs a certain incubation period, the nucleation point of bainite is more at the beginning of isothermal transformation, the content of bainite is increased along with the extension of isothermal time, if the heat preservation time is too short, the content of lower bainite is less, the heat preservation time is too long, the contents of martensite and residual austenite are less, the granular carbide after heat treatment is mainly nano-scale and is distributed in the crystal lattice of the structure where the martensite is located, compared with the larger granular carbide (spherical pearlite) before heat treatment, the size of the granular carbide after heat treatment is smaller, and the granular carbide after heat treatment is distributed in the crystal lattice.
Compared with the prior art, the invention has the advantages that: the heat treatment of the application can obviously change the complex phase structure composition of the spheroidized annealed high-carbon chromium steel after the heat treatment, and ensure that the final product has high strength, toughness and hardness. The heat treatment must be designed based on a spheroidized annealed structure and a chemical composition having a high hardenability property. After the treatment by the process method, the microstructure of the spheroidized annealed high-hardenability high-carbon chromium bearing steel is martensite, lower bainite, retained austenite and granular carbide, and the tensile strength R m 2230-2260 MPa, yield strength R p0.2 1360-1450 MPa, unnotched impact energy A K 130-140J and 60-62 HRC hardness.
Drawings
FIG. 1 is a microstructure before heat treatment, which is a microstructure of a material before heat treatment described in all examples and comparative examples;
FIG. 2 is a micrograph of particulate carbides in the microstructure shown in FIG. 1;
FIG. 3 is a schematic view of the isothermal quenching heat treatment process of the present application;
FIG. 4 is a microstructure of example 1;
FIG. 5 is a microstructure of example 2;
FIG. 6 is a microstructure of comparative example 1;
FIG. 7 is a microstructure of comparative example 2;
FIG. 8 is a microstructure of comparative example 3.
Detailed Description
The present invention is described in further detail below with reference to examples, which are intended to be illustrative and not to be construed as limiting the invention. The specification of the product in the embodiment is round steel with the diameter of 50mm, and the sampling position is the edge of the bar.
The high-carbon chromium steel in the embodiment comprises the following chemical components in percentage by mass: 1.0% C, 0.25% Mn, 1.70% Cr, 0.40% Mo, ni < 0.10%, ti < 0.002%, P < 0.005%, S < 0.005%, O < 0.001%, H < 0.0002%, the balance Fe and unavoidable impurities. The round steel product is obtained by smelting, casting and hot rolling of molten steel, the product is treated by spheroidizing annealing to obtain a fine and uniform spheroidized annealed structure, the average diameter of granular carbides is 0.40 mu m, the spacing between the granular carbides is 0.10-0.20 mu m, the hardness is 221HBW, and the microstructure is shown in figure 1 and figure 2.
Examples the heat treatment process parameters for the products are shown in table 1. The microstructure photographs after heat treatment are shown in FIGS. 4 and 5, and the mechanical properties are shown in Table 2. It can be seen that the microstructures of examples 1 and 2 consist essentially of lower bainite + martensite + particulate carbide + retained austenite after heat treatment. Example 1 after heat treatment had a tensile strength of 2236MPa, a yield strength of 1363MPa, an unnotched impact energy of 134J, and a hardness of 61.2HRC; example 2 after heat treatment had a tensile strength of 2245MPa, a yield strength of 1415MPa, an unnotched impact energy of 137J and a hardness of 61.6HRC. Therefore, after the heat treatment process, the microstructure of the spheroidized annealed high-hardenability high-carbon chromium steel is lower bainite, martensite, granular carbide and residual austenite, and because the relative contents of the lower bainite and the martensite cannot be distinguished by modern detection means, the content difference can be generally reflected only by the performance, and the tensile strength R m 2230-2260 MPa, yield strength R p0.2 1360-1450 MPa, unnotched impact energy A K 130-140J and 60-62 HRC hardness. Namely, the toughness and the hardness are obviously improved after the heat treatment.
The heat treatment process parameters used in comparative example 1 are shown in table 1. The microstructure photograph after heat treatment is shown in FIG. 6, and the mechanical properties are shown in Table 2. It can be seen that the microstructure of comparative example 1, which consists essentially of lower bainite + particulate carbides + retained austenite after heat treatment, promotes the formation of bainite due to the higher quench isotherm temperature, which is detrimental to the formation of subsequent air-cooled martensite. Comparative example 1 was heat treated to give a tensile strength of 2325MPa, a yield strength of 1897MPa, an unnotched impact energy of 161J and a hardness of 57.0HRC. Therefore, after the heat treatment process is adopted, the microstructure of the spheroidized annealed high-hardenability high-carbon chromium steel has no martensite structure, the hardness is relatively low, and the hardness of martensite formed in the spheroidized annealed high-carbon chromium steel is obviously improved.
The heat treatment process parameters used in comparative example 2 are shown in table 1. The microstructure photograph after heat treatment is shown in FIG. 7, and the mechanical properties are shown in Table 2. It can be seen that the microstructure of comparative example 2 after heat treatment consists essentially of lower bainite + particulate carbides + retained austenite, and since the heating temperature is low, the carbides are less dissolved into the matrix, the particulate carbides content is increased, and the formation of martensite is suppressed. Comparative example 2 has a tensile strength of 2164MPa, a yield strength of 1483MPa, an unnotched impact power of 98J, and a hardness of 59.7HRC after heat treatment. Therefore, after the heat treatment process, the microstructure of the spheroidized annealed high-hardenability high-carbon chromium steel has no martensite structure, and has low unnotched impact energy and hardness.
The heat treatment process parameters used in comparative example 3 are shown in table 1. The microstructure photograph after heat treatment is shown in FIG. 8, and the mechanical properties are shown in Table 2. It can be seen that the microstructure of comparative example 1 consists essentially of lower bainite + martensite + particulate carbide + retained austenite after heat treatment. However, because the austenitizing heating temperature is low, the dissolution of the grain carbide is less (the bright spots in the structure shown in fig. 8 are more, mainly caused by the less dissolution of the larger grain carbide), the larger grain carbide is easy to become the initiation point of the crack in the service process, and the toughness of the material after heat treatment is reduced. Comparative example 3 has a tensile strength of 2196MPa, a yield strength of 1079MPa, unnotched impact power of 83J and hardness of 62.0HRC after heat treatment. Therefore, after the heat treatment process, the yield strength and the unnotched impact power of the spheroidized annealed high-hardenability high-carbon chromium steel are both low.
TABLE 1 Heat treatment Process parameters used in the examples and comparative examples
| Numbering | Heating temperature (. Degree.C.) | Heating time (min/mm) | Isothermal temperature (. Degree. C.) | Heat preservation time (min/mm) |
| Example 1 | 880 | 2.5 | 200 | 30 |
| Example 2 | 880 | 3.0 | 200 | 30 |
| Comparative example 1 | 860 | 2.5 | 240 | 20 |
| Comparative example 2 | 840 | 2.5 | 200 | 20 |
| Comparative example 3 | 860 | 2.5 | 200 | 30 |
TABLE 2 microstructure composition and mechanical properties after heat treatment of examples and comparative examples
In addition to the above embodiments, the present invention also includes other embodiments, and any technical solutions formed by equivalent transformation or equivalent replacement should fall within the scope of the claims of the present invention.
Claims (8)
1. A heat treatment process of spheroidized annealed high-hardenability high-carbon chromium steel is characterized by comprising the following steps of: the microstructure of the high-carbon chromium steel before heat treatment is a spheroidized annealed structure, granular carbides are distributed on a ferrite matrix, and the first step is as follows: heating the high carbon chromium steel product to Ac cm Keeping the temperature in the temperature range of 30-50 ℃, wherein the heat preservation time is 1.5 min/mm-3.0 min/mm ﹡ d, and d is the diameter of the round steel or the longest straight line distance on the section of the product and is unit mm; step two: quenching the product after heat preservation in an alkali bath at 190-210 ℃, and quenching the product in the alkali bath to the bath temperature; step (ii) ofThirdly, the method comprises the following steps: and (3) preserving the heat of the product treated in the step (II) in an alkaline bath for 25-35 min/mm ﹡ d, wherein d is the diameter of the round steel or the longest straight line distance on the section of the product, and is unit mm, and then cooling the product away from the bath in air.
2. The heat treatment process of the spheroidized annealed high-hardenability high-carbon chromium steel according to claim 1, characterized in that: before heat treatment, the average diameter of the granular carbides of the spheroidizing annealed structure is 0.40 to 0.7 μm, and the pitch of the granular carbides is 0.10 to 0.20 μm.
3. The heat treatment process of the spheroidized annealed high-hardenability high-carbon chromium steel according to claim 1, characterized in that: the weight percentage of the elements of the high-carbon chromium steel meet C:0.95 to 1.05%, si:0.20 to 0.30%, mn: 0.60-0.80%, cr:1.65 to 1.75%, mo:0.40 to 0.50 percent.
4. The heat treatment process of the spheroidized annealed high-hardenability high-carbon chromium steel according to claim 1, characterized in that: in the first step, the heating temperature of the product is Ac cm Above 35 ℃.
5. The heat treatment process of the spheroidized annealed high-hardenability high-carbon chromium steel according to claim 1, characterized in that: in the second step, the temperature of the alkali bath is 200 ℃.
6. The heat treatment process of the spheroidized annealed high-hardenability high-carbon chromium steel according to claim 1, characterized in that: in the second step, the isothermal medium of the alkali bath is NaOH + KOH.
7. The heat treatment process of the spheroidized annealed high-hardenability high-carbon chromium steel according to claim 6, characterized in that: in step two, the isothermal medium of the alkaline bath is 37wt% NaOH +63wt% KOH.
8. The heat treatment process of the spheroidized annealed high-hardenability high-carbon chromium steel according to claim 1, characterized in that: after heat treatment, the product obtains a structure with hardening phase martensite on the basis of lower bainite, and residual austenite + granular carbides, wherein the whole structure is mainly the lower bainite, and the hardening phase martensite structure exists in a small amount.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202211324462.XA CN115595408A (en) | 2022-10-27 | 2022-10-27 | Heat treatment process of spheroidized annealed high-hardenability high-carbon chromium steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202211324462.XA CN115595408A (en) | 2022-10-27 | 2022-10-27 | Heat treatment process of spheroidized annealed high-hardenability high-carbon chromium steel |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN115595408A true CN115595408A (en) | 2023-01-13 |
Family
ID=84851596
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202211324462.XA Pending CN115595408A (en) | 2022-10-27 | 2022-10-27 | Heat treatment process of spheroidized annealed high-hardenability high-carbon chromium steel |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN115595408A (en) |
-
2022
- 2022-10-27 CN CN202211324462.XA patent/CN115595408A/en active Pending
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN105112774B (en) | The air-cooled hardening spring steel of the low middle carbon microalloy of high-strength tenacity and its shaping and Technology for Heating Processing | |
| CN101613835A (en) | A kind of alloy hot rolled steel plate and make the method for gas cylinder with it | |
| CN111893391A (en) | Nano bainite hot work die steel and preparation method thereof | |
| CN105088081B (en) | The manufacturing process of stabiliser bar | |
| JP5226083B2 (en) | High alloy cold die steel | |
| CN109609848A (en) | High tough antifatigue nano-scaled precipitate enhancing Ma-Austria's Multiphase Steel and preparation method thereof | |
| JP2010255095A (en) | Method for manufacturing bearing-component excellent in rolling fatigue characteristics under foreign matter environment | |
| CN109763078A (en) | A kind of heat-resisting alloy carburizing steel and preparation method thereof | |
| CN107916364B (en) | Hot work die steel | |
| CN102212760A (en) | Steel with high toughness and ultrahigh strength | |
| CN109763061A (en) | A kind of non-hardened and tempered steel and preparation method thereof | |
| CN109759779A (en) | A kind of non-hardened and tempered steel motor shaft and its processing method | |
| CN113862561A (en) | Long-life high-carbon bearing steel pipe and preparation method and application thereof | |
| JP4676993B2 (en) | Bush making | |
| CN109695003A (en) | A kind of high wear-resisting steel ball and its manufacturing method with excellent in toughness | |
| CN107794348A (en) | A kind of Technology for Heating Processing of raising Cr12MoV steel combination properties | |
| CN111733312B (en) | Heat treatment process for improving comprehensive mechanical property of H13 steel | |
| CN105714190A (en) | Steel for impact-resistant load bearing and heat treatment method of steel | |
| CN113718174A (en) | Double-refined high-strength-toughness long-life medium-high carbon bearing steel and preparation method thereof | |
| CN104087824B (en) | A kind of preparation method with the hyperfine structure bainitic steel of TRIP effect | |
| CN114717389B (en) | Wear-resistant low-temperature bainite hot work die steel and preparation method thereof | |
| CN109022710A (en) | The heat treatment method of nitrogenous plastic mould band steel | |
| CN109593921A (en) | The tufftride heat treatment method of mould steel | |
| CN107217211B (en) | A kind of flange disk-like accessory and its manufacturing method | |
| CN115595408A (en) | Heat treatment process of spheroidized annealed high-hardenability high-carbon chromium steel |
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 |