CN115505845A - Steel for rotary blade and production method - Google Patents
Steel for rotary blade and production method Download PDFInfo
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- CN115505845A CN115505845A CN202211172889.2A CN202211172889A CN115505845A CN 115505845 A CN115505845 A CN 115505845A CN 202211172889 A CN202211172889 A CN 202211172889A CN 115505845 A CN115505845 A CN 115505845A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- 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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
-
- 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
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
-
- 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
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
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- Organic Chemistry (AREA)
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- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The steel for the rotary blade comprises the following chemical components in percentage by weight: c:0.35 to 0.52%, si:0.10 to 0.40%, mn:0.80 to 1.30%, cr:0.10 to 0.50%, ti:0.01 to 0.05%, B:0.001 to 0.005 percent, less than or equal to 0.010 percent of P and less than or equal to 0.005 percent of S; the production method comprises the following steps: casting into a blank after smelting; heating a casting blank; hot rolling to product thickness; cooling; coiling; slowly cooling; carrying out water quenching treatment after forming; naturally cooling to room temperature. After the steel is processed and formed, and then is subjected to hot rolling and water quenching treatment, the structure of a formed product, namely a ploughing knife, is martensite, the hardness is 47-55 HRC, the wear resistance is excellent, and the minimum weight loss reaches 25g after ploughing for one hundred mu.
Description
Technical Field
The invention relates to steel for tools and a production method thereof, in particular to steel for a rotary blade and a production method thereof.
Background
The rotary tillage cutter is an important farmland soil-spreading part, loosens soil, returns straws to fields and the like in a rotating mode, is mainly made of 65Mn, 60Si2Mn and other steels, consumes over ten thousand tons of steel per year, and is most widely applied to 65 Mn. The main technical requirements of the steel for the rotary blade are to ensure the heat treatment quality, to achieve enough hardness and enough wear resistance of the product, and to prevent the product from generating large deformation, warping and breaking in the use process. The current common production process is as follows: the method comprises the steps of hot rolled plate blank making with the thickness of 6-12mm, heating, forming, quenching and tempering, and has the advantages of long production flow, high cost, easy generation of defects such as cracks, oxidation, decarburization and the like. Therefore, the development of the steel for the rotary blade which is easy to be thermally treated and has good wear resistance is urgent.
After retrieval: chinese patent application No. CN201611251565.2, which discloses an "agricultural ground rotary tillage blade alloy spring steel material", comprising, by mass, 0.50-0.70% of C, 0.70-1.00% of Mn, no more than 0.04% of P, no more than 0.04% of S, no more than 0.40% of Ni, no more than 0.30% of Cu, 1.00-1.50% of Si, 0.30-0.50% of Cr, and Fe. According to the agricultural flexible-ground rotary tillage alloy spring steel disclosed by the document, relevant components are finely adjusted, and Ti is added, so that the beneficial effect of nitrogen in the steel is effectively exerted, crystal grains are refined, and the toughness of the steel is improved; the content of Si is reduced, the content of Cr is increased, the toughness of the spring steel can be improved, and the problems of decarburization and grain coarsening during heating of 60Si2Mn can be solved. The carbon content of the steel grade is 0.50-0.70%, the steel grade belongs to the steel grade after fine adjustment of 60Si2Mn, and the steel grade is easy to break when water quenching is carried out.
The document with the Chinese patent application number of CN92108203.7 discloses a nodular cast iron rotary blade and a manufacturing method thereof, wherein the nodular cast iron is adopted as a material, and the manufacturing method comprises three procedures of sand casting, heat treatment and handle drilling. The heat treatment is a key process, and five schemes of high-temperature annealing, complete normalizing, partial austenitizing normalizing, isothermal quenching and thermal refining can be adopted. The key process can adopt five schemes of high-temperature annealing, complete normalizing, partial austenitizing normalizing, isothermal quenching and thermal refining. The rotary blade provided by the document has simple process, the mechanical property meets the requirement, the service life exceeds the index of 500 mu of 65Mn steel blade rotary soil, and the cost is only 60 percent of that of 65Mn steel blade. The material of the invention belongs to cast nodular cast iron, the production process is long, and the actual application is less at present.
The document with the Chinese patent application number of CN200910010157.1 discloses an energy-saving wear-resistant rotary blade and a production method thereof, and the method comprises the following process steps: taking a base material, welding tungsten carbide on the surface of the base material by adopting carbon dioxide gas shielded welding, heating the welded base material to 1000-1100 ℃ integrally, and then performing roll forming to obtain the tungsten carbide alloy. The working surface of the rotary blade is rolled with the wear-resistant layer, so that the service life of the rotary blade is prolonged, and a great number of experiments prove that one rotary blade in the document can be equivalent to the service life of 3-5 rotary blades in the past, thereby greatly reducing the energy waste and simultaneously reducing the use cost of farmers. The material of the invention belongs to a high-hardness material welded on the surface, has long production process and high cost, and needs special welding equipment.
Disclosure of Invention
The invention aims to overcome the defects of long process period and high energy consumption caused by quenching and tempering processes, even normalizing, in the prior art, and provides the steel for the rotary blade and the production method thereof, wherein the steel is only subjected to water quenching in the subsequent process, and has short production flow, high product hardness and excellent wear resistance.
The measures for realizing the aim are as follows:
the steel for the rotary blade comprises the following components in percentage by weight: c:0.35 to 0.52%, si:0.10 to 0.40%, mn: 0.80-1.30%, cr:0.10 to 0.50%, ti:0.01 to 0.05%, B:0.001 to 0.005 percent of the total weight of the alloy, less than or equal to 0.010 percent of P, less than or equal to 0.005 percent of S, and the balance of iron and inevitable impurities.
Preferably: the weight percentage content of C is 0.40-0.50%.
Preferably: the weight percentage content of Si is 0.18-0.36%.
Preferably: the weight percentage content of Mn is 0.90-1.20%.
Preferably: the weight percentage content of Ti is 0.02-0.04%.
Preferably: the weight percentage content of B is 0.002-0.004%.
A method for producing steel for a rotary blade comprises the following steps:
1) Casting into a blank after smelting, wherein: controlling the superheat degree of molten steel not to exceed 35 ℃, and controlling the thickness of continuous casting billet to be 200 to
240mm；
2) Heating the casting blank, and feeding the casting blank into a heating furnace before the complete austenite of the casting blank is converted, wherein the heating temperature is controlled to be 1100-1280 ℃, and the furnace time is 60-120 min;
3) Hot rolling to product thickness: controlling the finishing temperature to be 850-950 ℃;
4) Cooling to coiling temperature;
5) Coiling, and controlling the coiling temperature to be 580-655 ℃;
6) Slowly cooling, and cooling to room temperature at a cooling speed of less than or equal to 10 ℃/h;
7) And (3) water quenching treatment after forming: heating the formed part to 850-950 ℃, and keeping the temperature at the temperature of 15E
Performing water quenching and cooling to no more than 100 ℃ after 30 min;
8) Naturally cooling to room temperature.
The action and mechanism of each raw material and main process in the invention
C: carbon mainly plays a role in improving the strength and hardenability of steel in steel, carbon exists in a hot rolling structure in the form of carbide to form pearlite, bainite and the like, the carbon exists in a solid solution state after quenching, the structure is subjected to phase transformation strengthening, and the carbide is precipitated after tempering to play a role in precipitation strengthening. Too high carbon content decreases the plasticity and toughness of the steel, and too low carbon content decreases the hardenability of the steel, which is not favorable for the heat treatment of the saw blade, so it is limited to 0.35 to 0.52%, and preferably the content of C is 0.40 to 0.50% by weight.
Si: silicon enhances the strength of steel by solution strengthening and refining pearlite sheet spacing in steel, but reduces plasticity and toughness and increases surface defects of hot rolled sheet. Silicon is a main deoxidizer, and the content of silicon in steel is generally 0.1% or more, so that the content of Si is limited to 0.10 to 0.40%, preferably 0.18 to 0.36% by weight.
Mn: manganese acts in the steel to increase the strength of the steel, combines with S in the steel to form MnS, and eliminates the influence of the S element, and Mn is a good deoxidizer. However, since too high Mn content tends to cause slab center segregation during continuous casting and to degrade the homogeneity of the material, the Mn content is limited to 0.80 to 1.30%, preferably 0.90 to 1.20% by weight.
Cr: the chromium element can improve the strength, the hardenability and the tempering resistance and reduce the decarburized layer of the hot-rolled plate, but the chromium element can obviously increase the banded structure of the steel and influence the uniformity of the structure, so that the Cr content is controlled to be 0.10-0.50%.
Ti: titanium can form refractory carbide, structure grains are refined in the production process of steel grades, strength and toughness are improved, nitrogen elements in steel are fixed, loss of boron elements is reduced, the effect of improving hardenability of boron elements is fully exerted, the content of Ti is controlled to be 0.01-0.05%, and the content of Ti in percentage by weight is preferably 0.02-0.04%.
B: boron improves the hardenability of steel, improves the heat treatment performance, realizes key elements of water quenching, can properly reduce the carbon content and reduce the addition of Cr and Mn elements, and is an element with high price. In the invention, the content of B is controlled to be 0.001-0.005%, and the content of B in percentage by weight is preferably 0.002-0.004%.
The invention controls the casting blank to enter the heating furnace before the complete austenite transformation, the heating temperature is controlled to be 1100-1280 ℃, and the defects of casting blank cracks caused by the incomplete austenite transformation of the steel blank are prevented.
The invention controls the finishing temperature to be 850-950 ℃, because the crystal grains can be effectively refined at the temperature, the hot rolling difficulty is reduced, and the hot rolling defects are reduced.
The cooling speed is controlled to be less than or equal to 10 ℃/h, and the slow cooling and heat preservation can be effectively carried out on the hot rolled steel coil at the speed, so that the hot rolling state strength is reduced, and the subsequent processing process is facilitated.
The invention heats the formed part to 850-950 ℃, keeps the temperature for 15-30 min at the temperature, and then carries out water quenching and cooling to be not more than 100 ℃ because the formed part needs to be fully austenitized before quenching, thereby preventing the carbide from being undissolved and reducing the strength and the performance after heat treatment.
Compared with the prior art, after the steel is processed and formed, and then is subjected to hot rolling and water quenching treatment, the structure of the formed product, namely the tillage knife, is martensite, the hardness is 47-55 HRC, the wear resistance is excellent, and the minimum weight loss reaches 25g after one hundred acres of farmland.
Drawings
FIG. 1 shows the metallographic structure (pearlite + ferrite) of a hot rolled steel sheet according to the present invention;
FIG. 2 shows the metallographic structure (martensite) of the steel of the present invention after water quenching.
Detailed Description
The present invention is described in detail below:
table 1 is a list of chemical compositions for each example of the present invention and comparative example;
table 2 is a table of the main process parameters of each example of the present invention and comparative example;
table 3 is a table of the performance test of each example and comparative example of the present invention.
The examples of the invention were produced as follows
1) Casting into a blank after smelting, wherein: controlling the superheat degree of molten steel not to exceed 35 ℃ and controlling the thickness of a continuous casting billet to be 200-240 mm;
2) Heating the casting blank, and feeding the casting blank into a heating furnace before the complete austenite of the casting blank is converted, wherein the heating temperature is controlled to be 1100-1280 ℃, and the furnace time is 60-120 min;
3) Hot rolling to product thickness: controlling the finishing temperature to be 850-950 ℃;
4) Cooling to the coiling temperature;
5) Coiling, and controlling the coiling temperature to be 580-655 ℃;
6) Slowly cooling, and cooling to room temperature at a cooling speed of less than or equal to 10 ℃/h;
7) And (3) water quenching treatment after forming: heating the formed part to 850-950 ℃, preserving heat for 15-30 min at the temperature, and then carrying out water quenching and cooling to be not more than 100 ℃;
8) And naturally cooling to room temperature.
TABLE 1 list of chemical compositions (wt%) of inventive and comparative examples
Table 2 list of main process parameters of various embodiments of the present invention
TABLE 3 test result list of mechanical properties of each example and comparative example of the present invention
As can be seen from Table 3, the improvement of the strength can effectively reduce the abrasion and weight loss, but the too high strength can cause the rotary blade to be easy to break, and the invention solves the problems of easy cracking of water quenching and easy breaking in use by refining crystal grains, thereby not only simplifying the production process, but also improving the service life of the material.
The present embodiments are merely preferred examples, and are not intended to limit the scope of the present invention.
Claims (7)
1. The steel for the rotary blade comprises the following components in percentage by weight: c:0.35 to 0.52%, si:0.10 to 0.40%, mn: 0.80-1.30%, cr:0.10 to 0.50%, ti:0.01 to 0.05%, B:0.001 to 0.005 percent of iron, less than or equal to 0.010 percent of P, less than or equal to 0.005 percent of S, and the balance of iron and inevitable impurities.
2. The steel for rotary blades of claim 1, which comprises: the weight percentage content of C is 0.40-0.50%.
3. The steel for rotary blade according to claim 1, wherein: the weight percentage content of Si is 0.18-0.36%.
4. The steel for rotary blade according to claim 1, wherein: the weight percentage content of Mn is 0.90-1.20%.
5. The steel for rotary blades of claim 1, which comprises: the weight percentage content of Ti is 0.02-0.04%.
6. The steel for rotary blade according to claim 1, wherein: the weight percentage content of B is 0.002-0.004%.
7. A method of producing a steel for rotary blade according to claim 1, comprising the steps of:
1) Casting into a blank after smelting, wherein: controlling the superheat degree of molten steel not to exceed 35 ℃ and controlling the thickness of a continuous casting billet to be 200-240 mm;
2) Heating the casting blank, and feeding the casting blank into a heating furnace before the complete austenite transformation of the casting blank, wherein the heating temperature is controlled to be 1100-1280 ℃, and the furnace time is 60-120 min;
3) Hot rolling to product thickness: controlling the finishing temperature to be 850-950 ℃;
4) Cooling to coiling temperature;
5) Coiling, and controlling the coiling temperature to be 580-655 ℃;
6) Slowly cooling to room temperature at a cooling speed of less than or equal to 10 ℃/h;
7) And (3) water quenching treatment after forming: heating the formed part to 850-950 ℃, preserving heat for 15-30 min at the temperature, and then carrying out water quenching and cooling to be not more than 100 ℃;
8) Naturally cooling to room temperature.
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| Application Number | Priority Date | Filing Date | Title |
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| CN202211172889.2A CN115505845A (en) | 2022-09-26 | 2022-09-26 | Steel for rotary blade and production method |
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| Application Number | Priority Date | Filing Date | Title |
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| CN202211172889.2A CN115505845A (en) | 2022-09-26 | 2022-09-26 | Steel for rotary blade and production method |
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Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107723601A (en) * | 2017-11-01 | 2018-02-23 | 山东钢铁股份有限公司 | A kind of residual stress is 50 100MPa wear-resisting steel plate and preparation method thereof |
| CN107779577A (en) * | 2016-08-26 | 2018-03-09 | 鞍钢股份有限公司 | Gardening tool steel with excellent processability and production method thereof |
| CN108085594A (en) * | 2017-12-20 | 2018-05-29 | 代超群 | Agricultural ploughing machine wear-out part special-purpose steel and its production technology |
| CN108660374A (en) * | 2018-05-23 | 2018-10-16 | 山东钢铁股份有限公司 | A kind of quenching aligning short route wear-resisting steel plate and preparation method thereof |
| CN111593264A (en) * | 2020-06-28 | 2020-08-28 | 武汉钢铁有限公司 | Tempering-free wear-resistant hot-rolled strip steel and production method thereof |
-
2022
- 2022-09-26 CN CN202211172889.2A patent/CN115505845A/en active Pending
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107779577A (en) * | 2016-08-26 | 2018-03-09 | 鞍钢股份有限公司 | Gardening tool steel with excellent processability and production method thereof |
| CN107723601A (en) * | 2017-11-01 | 2018-02-23 | 山东钢铁股份有限公司 | A kind of residual stress is 50 100MPa wear-resisting steel plate and preparation method thereof |
| CN108085594A (en) * | 2017-12-20 | 2018-05-29 | 代超群 | Agricultural ploughing machine wear-out part special-purpose steel and its production technology |
| CN108660374A (en) * | 2018-05-23 | 2018-10-16 | 山东钢铁股份有限公司 | A kind of quenching aligning short route wear-resisting steel plate and preparation method thereof |
| CN111593264A (en) * | 2020-06-28 | 2020-08-28 | 武汉钢铁有限公司 | Tempering-free wear-resistant hot-rolled strip steel and production method thereof |
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