CN112605137A - Production method of medium-carbon martensitic stainless steel - Google Patents
Production method of medium-carbon martensitic stainless steel Download PDFInfo
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- CN112605137A CN112605137A CN202011223698.5A CN202011223698A CN112605137A CN 112605137 A CN112605137 A CN 112605137A CN 202011223698 A CN202011223698 A CN 202011223698A CN 112605137 A CN112605137 A CN 112605137A
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- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
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Abstract
The invention relates to a production method of medium-carbon martensitic stainless steel, which comprises the working procedures of billet heating, rolling control and cooling control and is characterized in that in the billet heating working procedure, a billet is heated by a regenerative heating furnace in sections, and the heating temperature of a heating section is 1130-1180 ℃, and the heating temperature of a soaking section is 1150-1200 ℃ from the inlet to the outlet of the heating furnace. The invention omits the process of slow cooling after rolling the medium carbon martensitic stainless steel, ensures the high quality of the steel on the basis of ensuring the cracking of the steel surface due to stress concentration when no cooling is carried out, and meets the requirements of steel and iron situations with low energy consumption and green production. The invention does not need to increase equipment and investment, does not increase production cost, fully utilizes the existing equipment and process, and overcomes the defects of high cost, long slow cooling period and incapability of continuous production of the slow cooling process.
Description
Technical Field
The invention belongs to the technical field of steel wire rolling, and particularly relates to a production method of medium-carbon martensitic stainless steel.
Background
The medium-carbon martensitic stainless steels 2Cr13 and 3Cr13 have good hardenability, and the high-temperature austenite can be completely quenched under the air cooling condition to obtain a lath martensite structure.
2Cr13 and 3Cr13 are mainly used for producing shaft and shaft sleeve products of washing machines. With the increase of domestic washing machine sales and the increase of washing machine outlets, the demand of the domestic washing machine sales is greatly increased.
In the production process of the medium-carbon martensitic stainless steel, because the components contain a large amount of chromium elements which are easy to form carbides, the cooling C curve of the medium-carbon martensitic stainless steel is shifted to the right, so that the supercooling stability of the medium-carbon martensitic stainless steel in an austenite state is increased, and the critical cooling speed is reduced. After the martensitic stainless steel is rolled at a high temperature and reaches required dimensional accuracy, slow cooling is generally adopted to prevent stress cracking during martensitic structure. When austenite is transformed to martensite, larger structure stress is generated, the generation of stress cracks on the surface of the wire rod is promoted and aggravated, and the fracture problem is generated in the process of packaging, transporting and storing the wire rod.
Therefore, after the medium-carbon martensitic stainless steel wire rod is rolled, slow cooling is required before an annealing process, so that the internal stress in the cooling process of the finished wire rod is eliminated, and the generation of surface stress cracks of the wire rod is reduced or eliminated. And for the medium-carbon martensitic stainless steel wire, slow cooling measures are adopted after hot rolling. And develops new processes such as slow cooling after rolling, waste heat treatment and the like.
In domestic stainless steel production plants, high-temperature spinning and hot coiling are generally adopted, and the hot coiled stainless steel quickly enters a heat-preservation pit with a gas heating function for slow cooling so as to effectively prevent the surface cracks of medium-carbon martensitic stainless steel.
Because the medium carbon martensitic stainless steel must be slowly cooled after being cooled at high temperature to eliminate the stress cracks on the surface of the steel, the current domestic patent on the stress crack resistance and slow cooling-free process is rarely reported: application No. 201810446681.2 discloses a method for producing an ultra-low carbon martensitic stainless steel medium plate, which mainly comprises the steps of stacking and slowly cooling a rolled steel plate to 300-500 ℃ on line, paving a bottom cover with a hot steel plate, wherein the slow cooling time is not less than 36 hours, and the slow cooling process needs to be selected and continued for 36 hours.
The above patent mainly guarantees the stress cracking problem of the martensitic stainless steel after high-temperature rolling through a slow cooling process, increases the production cost and the production period, and cannot realize the high-efficiency rolling production of high-speed wires. How to meet the requirement of high-efficiency rolling of the wire rod and ensure no stress cracks on the surface of the wire rod, is used for supporting mass production of medium-carbon martensitic stainless steel in China at low cost, and is a problem to be solved urgently.
Disclosure of Invention
The invention aims to solve the technical problem of providing a production method of medium-carbon martensitic stainless steel, which omits a slow cooling process when the medium-carbon martensitic stainless steel is produced and simultaneously ensures that the surface of steel has no stress cracks when being cooled.
In order to solve the technical problems, the technical scheme adopted by the invention is as follows: the production method of the medium-carbon martensitic stainless steel comprises the processes of billet heating, rolling control and cooling control, and is characterized in that in the billet heating process, a billet is heated in a heat accumulating type heating furnace in a segmented mode, a preheating section, a heating section and a soaking section are sequentially arranged from an inlet to an outlet of the heating furnace, the heating temperature of the heating section ranges from 1130 ℃ to 1180 ℃, and the heating temperature of the soaking section ranges from 1150 ℃ to 1200 ℃.
Further, the total heating time of the steel billet in the heating furnace is 2-3 h.
Furthermore, the residual oxygen amount of the heating furnace is controlled to be less than or equal to 6 percent.
Furthermore, the rolling procedure is controlled, the sizing temperature is reduced to 900-950 ℃, and the spinning temperature is 800-850 ℃.
Further, the cooling process is controlled, the stelmor roller way fan is completely closed, the heat preservation cover is completely closed, and the cooling speed of the stelmor roller way wire rod is 0.5-1.5 ℃/s.
From the composition and TTT curve of the martensitic stainless steel, the hypoeutectoid steel still belongs to the range of hypoeutectoid steel, so that proeutectoid ferrite is firstly precipitated when the temperature is lowered for transformation. From the high temperature plasticity curve, the brittle region of "V" shape is shown in the range of about 650 ℃ to 1000 ℃. The reason is similar to that of low-carbon cold heading steel, that is, the precipitation of carbon and nitride causes low-temperature brittleness of austenite with the decrease of temperature. At the same time, a small amount of proeutectoid ferrite precipitates and is distributed in a thin film form at the boundary of austenite, and a large difference in strength between ferrite and austenite results in generation and propagation of micro-cracks and voids in the thin film ferrite during stretching. The two factors together cause the medium carbon martensitic stainless steel to present a V-shaped brittleness area in the range of 650 ℃ to 1000 ℃. And along with the reduction of the temperature, the ferrite becomes thicker and the pearlite is precipitated, so that the modification coordination is improved, and the plasticity of the material is enhanced.
The medium carbon martensitic stainless steel has surface crack defects regularly distributed at the corners of the steel on both sides of the roll gap. This is because the metal at the roll gap is subjected to tensile stress which increases with the degree of non-uniform deformation and remains during deformation due to the low recrystallization rate in stainless steel. If the cooling speed after rolling is higher, the structure stress is generated during the martensite transformation, and the two stresses cause cooling cracks near the roll gap of the steel.
The method adopts the principle that the heating process of the medium-carbon martensitic stainless steel is improved, the stability of the steel after austenitizing is reduced, the possibility of the steel being transformed into martensite in the subsequent rolling and cooling process is reduced, the proportion of pearlite in the structure is increased, the generated structure stress is smaller, and the possibility of generating cooling cracks on the surface of the steel is low.
The purpose of the further reducing sizing temperature setting is to further reduce the likelihood that the wire rod will become martensitic during the subsequent rolling cooling.
The parameters of the spinning temperature and the stelmor roller bed are set to further transform a part of the structure of the wire rod to pearlite in the cooling process, increase the proportion of the pearlite in the structure, and reduce the generated structure stress, thereby reducing the possibility of generating cooling cracks on the surface of the steel material.
The invention aims to eliminate stress cracking on the surface of steel in the cooling process while eliminating the slow cooling process by reducing the sizing temperature, the spinning temperature and the stelmor roller table parameter setting.
Adopt the produced beneficial effect of above-mentioned technical scheme to lie in:
the invention omits the process of slow cooling after rolling the medium carbon martensitic stainless steel, ensures the high quality of the steel on the basis of ensuring no stress cracking on the surface of the steel, and meets the requirements of steel and iron situations with low energy consumption and green production. The invention does not need to increase equipment and investment, does not increase production cost, fully utilizes the existing equipment and process, and overcomes the defects of high cost, long slow cooling period and incapability of continuous production of the slow cooling process.
Drawings
FIG. 1 is a metallographic photograph of a carbon stainless steel wire rod in example 1
FIG. 2 is a photograph showing the grain size of the structure of the carbon stainless steel wire rod in example 1
FIG. 3 is a photograph showing the grain size of the structure of the carbon stainless steel wire rod in example 2
FIG. 4 is a photograph showing the grain size of the structure of the carbon stainless steel wire rod in example 3
FIG. 5 is a photograph showing the grain size of the structure of the carbon stainless steel wire rod in example 4.
Detailed Description
In order to make the objects, technical solutions and advantages of the present invention more apparent, the present invention is further described in detail with reference to the following embodiments. It should be understood that the specific embodiments described herein are merely illustrative of the invention and are not intended to limit the invention.
In order to better illustrate the invention, the following examples are given by way of further illustration.
Example 1
The production steel grade is 2Cr13, the production process comprises the steps of billet heating, rolling control, cooling control and billet heating, the billet is heated by a heat accumulating type heating furnace in a segmented mode, a preheating section, a heating section and a soaking section are sequentially arranged from the inlet to the outlet of the heating furnace, the heating temperature of the heating section is 1130 ℃, the heating temperature of the soaking section is 1150 ℃, the total heating time of the billet in the heating furnace is 2 hours, and the residual oxygen content of the heating furnace is controlled to be 2%. The rolling process is controlled, the sizing temperature is reduced to 900 ℃, and the spinning temperature is 800 ℃. And controlling the cooling process, wherein the stelmor roller way fan is fully closed, the heat preservation cover is fully closed, and the cooling speed of the stelmor roller way wire rod is 0.5 ℃/s.
Example 2
The production steel grade is 3Cr13, the production process comprises the steps of heating steel billets, controlling rolling, controlling cooling and heating the steel billets, the steel billets are heated by a regenerative heating furnace in sections, a preheating section, a heating section and a soaking section are sequentially arranged from the inlet to the outlet of the heating furnace, the heating temperature of the heating section is 1180 ℃, the heating temperature of the soaking section is 1200 ℃, the total heating time of the steel billets in the heating furnace is 3 hours, and the residual oxygen content of the heating furnace is controlled at 6%. The rolling process is controlled, the sizing temperature is reduced to 950 ℃, and the spinning temperature is 850 ℃. And controlling the cooling process, wherein the stelmor roller way fan is fully closed, the heat preservation cover is fully closed, and the cooling speed of the stelmor roller way wire rod is 1.5 ℃/s.
Example 3
The production steel grade is 2Cr13, the production process comprises the steps of billet heating, rolling control, cooling control and billet heating, the billet is heated by a regenerative heating furnace in sections, the preheating section, the heating section and the soaking section are sequentially arranged from the inlet to the outlet of the heating furnace, the heating temperature of the heating section is 1150 ℃, the heating temperature of the soaking section is 1170 ℃, the total heating time of the billet in the heating furnace is 2.6 hours, and the residual oxygen content of the heating furnace is controlled to be 3%. The rolling process is controlled, the sizing temperature is reduced to 930 ℃, and the spinning temperature is 830 ℃. And controlling the cooling process, wherein the stelmor roller way fan is fully closed, the heat preservation cover is fully closed, and the cooling speed of the stelmor roller way wire rod is 1.2 ℃/s.
Example 4
The production steel grade is 3Cr13, the production process comprises the steps of heating steel billets, rolling control, cooling control and heating steel billets, the steel billets are heated by a regenerative heating furnace in sections, a preheating section, a heating section and a soaking section are sequentially arranged from the inlet to the outlet of the heating furnace, the heating temperature of the heating section is 1140 ℃, the heating temperature of the soaking section is 1159 ℃, the total heating time of the steel billets in the heating furnace is 2.3 hours, and the residual oxygen content of the heating furnace is controlled to be 4%. The rolling process is controlled, the sizing temperature is reduced to 910 ℃, and the spinning temperature is 840 ℃. And controlling the cooling process, wherein the stelmor roller way fan is fully closed, the heat preservation cover is fully closed, and the cooling speed of the stelmor roller way wire rod is 0.7 ℃/s.
Example 5
The production steel grade is 2Cr13, the production process comprises the steps of heating steel billets, controlling rolling, controlling cooling and heating the steel billets, the steel billets are heated by a regenerative heating furnace in sections, a preheating section, a heating section and a soaking section are sequentially arranged from the inlet to the outlet of the heating furnace, the heating temperature of the heating section is 1159 ℃, the heating temperature of the soaking section is 1189 ℃, the total heating time of the steel billets in the heating furnace is 2.1h, and the residual oxygen content of the heating furnace is controlled to be 2.5%. The rolling process is controlled, the sizing temperature is reduced to 919 ℃, and the spinning temperature is 809 ℃. And controlling the cooling process, wherein the stelmor roller way fan is fully closed, the heat preservation cover is fully closed, and the cooling speed of the stelmor roller way wire rod is 0.9 ℃/s.
Example 6
The production steel grade is 3Cr13, the production process comprises the steps of heating steel billets, controlling rolling, controlling cooling and heating the steel billets, the steel billets are heated by a regenerative heating furnace in sections, the heating temperature of the heating section is 1169 ℃, the heating temperature of the soaking section is 1180 ℃, the total heating time of the steel billets in the heating furnace is 2.9 hours, and the residual oxygen content of the heating furnace is controlled at 5%. The rolling process is controlled, the sizing temperature is reduced to 939 ℃, and the spinning temperature is 819 ℃. And controlling the cooling process, wherein the stelmor roller way fan is fully closed, the heat preservation cover is fully closed, and the cooling speed of the stelmor roller way wire rod is 1.4 ℃/s.
The wire rods of 2Cr13 and 3Cr13 rolled in the examples 1-6 are subjected to low-power pickling according to national inspection standards, the surfaces of the wire rods have no stress cracks, the metallographic picture of the wire rod of the example 1 is shown in a figure 1, and the grain size picture of the finished wire rod rolled in the examples 1-4 is shown in figures 2-5.
Although the present invention has been described in detail with reference to the above embodiments, it should be understood by those skilled in the art that: modifications and equivalents may be made thereto without departing from the spirit and scope of the invention and it is intended to cover in the claims the invention as defined in the appended claims.
Claims (5)
1. The production method of the medium-carbon martensitic stainless steel comprises the processes of billet heating, rolling control and cooling control, and is characterized in that in the billet heating process, a billet is heated in a heat accumulating type heating furnace in a segmented mode, a preheating section, a heating section and a soaking section are sequentially arranged from an inlet to an outlet of the heating furnace, the heating temperature of the heating section ranges from 1130 ℃ to 1180 ℃, and the heating temperature of the soaking section ranges from 1150 ℃ to 1200 ℃.
2. The method for producing a medium-carbon martensitic stainless steel as claimed in claim 1 wherein the total heating time of the steel billet in the heating furnace is 2-3 hours.
3. The method for producing a medium-carbon martensitic stainless steel as claimed in claim 1, wherein the residual oxygen content of the heating furnace is controlled to 6% or less.
4. The method for producing the medium-carbon martensitic stainless steel as claimed in claim 1, wherein the rolling process is controlled so that the diameter reduction temperature is 900 to 950 ℃ and the spinning temperature is 800 to 850 ℃.
5. The method for producing the medium-carbon martensitic stainless steel as claimed in claim 1, wherein the controlled cooling process comprises the steps of fully turning off a stelmor roller fan, fully turning off a heat-insulating cover and cooling the stelmor roller wire at a speed of 0.5-1.5 ℃/s.
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| CN202011223698.5A CN112605137A (en) | 2020-11-05 | 2020-11-05 | Production method of medium-carbon martensitic stainless steel |
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114247750A (en) * | 2021-11-17 | 2022-03-29 | 邢台钢铁有限责任公司 | Process for improving stress cracks of medium-carbon alloy cold forging steel hot rolled blank |
Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH1085801A (en) * | 1996-09-09 | 1998-04-07 | Sumitomo Metal Ind Ltd | Blooming method for cast billet of martensitic stainless steel |
| CN105525226A (en) * | 2014-09-29 | 2016-04-27 | 宝钢特钢有限公司 | Martensitic stainless steel wire rod and production method thereof |
| CN106077084A (en) * | 2016-06-24 | 2016-11-09 | 江苏省沙钢钢铁研究院有限公司 | High-speed wire rolling method for austenitic stainless steel wire rod |
| CN106591734A (en) * | 2016-11-30 | 2017-04-26 | 邢台钢铁有限责任公司 | High-strength martensitic stainless steel wire rod and production method thereof |
| CN106623417A (en) * | 2016-12-22 | 2017-05-10 | 常熟理工学院 | High speed wire rolling method for austenitic stainless steel wire rod for welding |
| CN109055692A (en) * | 2018-10-15 | 2018-12-21 | 江苏省沙钢钢铁研究院有限公司 | Annealing-free dual-phase steel wire rod for pressure container and production method thereof |
| CN111485086A (en) * | 2020-04-08 | 2020-08-04 | 中天钢铁集团有限公司 | Controlled rolling and cooling process for reducing decarburized layer depth of high-carbon alloy tool steel wire rod |
| CN111530925A (en) * | 2020-04-21 | 2020-08-14 | 邢台钢铁有限责任公司 | Rolling method of high-strength automobile spring steel wire rod |
-
2020
- 2020-11-05 CN CN202011223698.5A patent/CN112605137A/en not_active Withdrawn
Patent Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH1085801A (en) * | 1996-09-09 | 1998-04-07 | Sumitomo Metal Ind Ltd | Blooming method for cast billet of martensitic stainless steel |
| CN105525226A (en) * | 2014-09-29 | 2016-04-27 | 宝钢特钢有限公司 | Martensitic stainless steel wire rod and production method thereof |
| CN106077084A (en) * | 2016-06-24 | 2016-11-09 | 江苏省沙钢钢铁研究院有限公司 | High-speed wire rolling method for austenitic stainless steel wire rod |
| CN106591734A (en) * | 2016-11-30 | 2017-04-26 | 邢台钢铁有限责任公司 | High-strength martensitic stainless steel wire rod and production method thereof |
| CN106623417A (en) * | 2016-12-22 | 2017-05-10 | 常熟理工学院 | High speed wire rolling method for austenitic stainless steel wire rod for welding |
| CN109055692A (en) * | 2018-10-15 | 2018-12-21 | 江苏省沙钢钢铁研究院有限公司 | Annealing-free dual-phase steel wire rod for pressure container and production method thereof |
| CN111485086A (en) * | 2020-04-08 | 2020-08-04 | 中天钢铁集团有限公司 | Controlled rolling and cooling process for reducing decarburized layer depth of high-carbon alloy tool steel wire rod |
| CN111530925A (en) * | 2020-04-21 | 2020-08-14 | 邢台钢铁有限责任公司 | Rolling method of high-strength automobile spring steel wire rod |
Non-Patent Citations (1)
| Title |
|---|
| 线材生产编写组: "《线材生产》", 31 January 1983 * |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114247750A (en) * | 2021-11-17 | 2022-03-29 | 邢台钢铁有限责任公司 | Process for improving stress cracks of medium-carbon alloy cold forging steel hot rolled blank |
| CN114247750B (en) * | 2021-11-17 | 2024-01-23 | 邢台钢铁有限责任公司 | Process for improving stress crack of medium carbon alloy cold heading steel hot rolled blank |
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Application publication date: 20210406 |