CN118639093B - Anti-stripping roll materials and heat treatment process for high-speed wire pre-finishing mill - Google Patents
Anti-stripping roll materials and heat treatment process for high-speed wire pre-finishing mill Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C37/00—Cast-iron alloys
- C22C37/04—Cast-iron alloys containing spheroidal graphite
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B27/00—Rolls, roll alloys or roll fabrication; Lubricating, cooling or heating rolls while in use
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
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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
- C21D5/00—Heat treatments of cast-iron
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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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/38—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for roll bodies
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C37/00—Cast-iron alloys
- C22C37/06—Cast-iron alloys containing chromium
- C22C37/08—Cast-iron alloys containing chromium with nickel
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C37/00—Cast-iron alloys
- C22C37/10—Cast-iron alloys containing aluminium or 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
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Abstract
本发明涉及轧辊铸造技术领域，更具体的涉及高线预精轧机组防剥落轧辊材料及热处理工艺。高线预精轧机组防剥落轧辊材料的化学组分包括：C、Si、Mn、Cr、Ni、Mo、V、W、Nb、Fe和不可避免杂质；轧辊材料的热处理工艺包括退火和淬火回火，其中淬火回火步骤包括：第一次升温保温、第二次升温保温、第三次升温保温、喷雾淬火和高温回火。本发明采用新材料及其热处理工艺制备的新材料高性能轧辊材料，解决原材料轧辊使用寿命短和常出现剥落等问题，提高了生产效率，降低了生产成本，具有较好的推广应用前景。
The present invention relates to the field of roller casting technology, and more specifically to an anti-stripping roller material and a heat treatment process for a high-speed wire pre-finishing mill. The chemical components of the anti-stripping roller material for a high-speed wire pre-finishing mill include: C, Si, Mn, Cr, Ni, Mo, V, W, Nb, Fe and unavoidable impurities; the heat treatment process of the roller material includes annealing and quenching and tempering, wherein the quenching and tempering steps include: a first heating and heat preservation, a second heating and heat preservation, a third heating and heat preservation, spray quenching and high-temperature tempering. The present invention adopts a new material and a high-performance roller material prepared by a new material and a heat treatment process thereof, which solves the problems of short service life and frequent spalling of raw material rollers, improves production efficiency, reduces production costs, and has a good prospect for promotion and application.
Description
Technical Field
The invention relates to the technical field of roller casting, in particular to an anti-stripping roller material of a high-speed wire pre-finishing mill group and a heat treatment process.
Background
The high-speed wire rod rolling mill has the characteristics of high rolling speed, high quality, high efficiency and the like, and provides guarantee conditions for high product yield and large range of product specifications. In recent years, a wire rod production line adopts a short stress line rolling mill, and a way of development of high speed, no torsion and no tension is adopted to develop endless rolling and low temperature rolling technologies; as the specifications of wire and bar products are more diversified, the demands of small-size products are continuously increased, and the mechanical properties of the processing tools are continuously improved, the mechanical properties of the processing tools are required to be continuously improved, and the high-speed wire production line realizes full-line low-temperature tapping and low-temperature controlled rolling, the microstructure, yield strength and toughness of the obtained products are simultaneously improved.
At present, the roller for the front section of the high-speed wire pre-finish rolling is mainly made of traditional high-nickel-chromium bainite ductile iron, and recent use conditions show that the roller is poor in wear resistance, anti-stripping performance and other accident resistance, the roller groove surface is not wear-resistant, stripping and blocking are carried out, pits are low in single-groove rolling quantity, the number of times of roller changing frequently becomes the bottleneck for further improving the productivity, and along with the development of a rolling mill towards high speed and high quality, the material roller is low in single-time service life due to the defects, and the production efficiency of a production line is influenced. This requires a significant increase in the spalling resistance and wear resistance of the working layer of the prefinishing mill train rolls while maintaining a good toughness of the substrate.
The prior art CN91107234.9 discloses a vanadium-titanium infinite chilled ductile iron roller and a casting method, the chemical components of the roller do not contain noble alloy elements such as Ni, cr, mo, cu, and the like, during casting, a mixed nodulizer composed of rare earth magnesium and an iron-magnesium mechanism nodulizer is used, and the produced roller has the characteristics of low cost, high hardness, good wear resistance and high strength, but does not contain the noble alloy elements such as Ni, cr, mo, cu, and the like, so that the cost can be reduced, but the mechanical property, the excessive steel amount and the wear resistance of the roller can be negatively influenced to a certain extent, and the prior art CN201410085918 discloses a manufacturing method of a free-cutting high-speed steel roller for centrifugal casting, wherein the processing technology discloses degradation, quenching and tempering technology, heat treatment process and the like, and the heat treatment process is complex, the heating speed is slow, the production period is long, and the application range of the technology is influenced.
The roll materials of the rough rolling frame of the wire rod and section mill are generally pearlite ductile iron, and the phenomena of deep crack of a rolling groove, large single steel passing amount, large turning amount, large hardness drop and the like exist in the using process.
Disclosure of Invention
In order to solve the technical problem, the first aspect of the invention provides an anti-stripping roll material of a high-speed wire pre-finishing mill group, wherein the chemical components of the roll material comprise C, si, mn, cr, ni, mo, V, W, nb, fe and unavoidable impurities.
Preferably, the mass percentage of V, mo and W satisfies the condition that V+Mo+W/2=1.9-4.5%.
Further preferably, the chemical composition of the roll material comprises, by mass, 2.6 to 3.6% of C, 1.3 to 2.0% of Si, 0.5 to 0.8% of Mn, 1.5 to 3.0% of Cr, 1.0 to 2.5% of Ni, 0.2 to 0.8% of Mo, 1.5 to 3.2% of V, 0.5 to 1.0% of W, 0.12 to 0.25% of Nb, and the balance of Fe and unavoidable impurities.
The elements in the roller of the invention have the following functions in the roller:
c (carbon) is the most basic element in the roller material alloy, the content of the C determines the quantity of carbide, the relative quantity of M 7C3 type carbide and total carbide, hardness, toughness, hardenability of the material and the like, and the related test results show that the content of the C in the roller is controlled to be 2.6-3.6wt% in the invention.
The Si element can induce bainite nucleation in the alloy matrix of the roller material and improve the nucleation rate. The Si can refine eutectic cells, increase austenitizing temperature and increase supercooling degree delta T of austenite transformation, and small nuclear embryos generated in the austenite can be used as a bainite core and a martensite core; according to the different powers of bainite and martensite nucleation, the design of a heat treatment process is improved, and the contents of the bainite and the martensite are controlled. The test result shows that the Si element can better induce bainite transformation, refine the bainitic structure and improve the hardness and the toughness. On the other hand, silicon is an element which strongly promotes graphitization and inhibits carbide precipitation, and the increase of the silicon quantity ensures that ductile iron is inoculated sufficiently, so that graphite with a large quantity and tiny and round shape is obtained, namely eutectic cells are refined, and bainite tissues are also refined. Therefore, the Si content is preferably controlled to 1.3 to 2.0 wt%.
When the Mn content is unchanged, the Mn content is properly reduced to improve the comprehensive mechanical property of the bainite, and mainly because Mn is a positive segregation element, the austenitizing temperature is reduced, the carbon content in the austenite is increased, the activity of carbon is reduced, the austenite is stabilized, the transformation of the bainite is dragged, and Si is a negative segregation element, the austenitizing temperature is improved, the activity of carbon is increased, the transformation of the bainite is complete, and the performance is improved. The research result shows that the matrix structure is fine needle-shaped bainite structure after Mn is added, but with the increase of Mn content, the segregation of Mn in the structure is serious, the quantity of martensite at the grain boundary is increased, and carbide is distributed along the grain boundary, the quantity is increased, which leads to the reduction of toughness, so that the addition quantity of Mn is controlled below 0.8wt%, and the addition quantity of Mn is preferably 0.5-0.8wt% in the invention.
Cr (Cr) is the most important element in the alloy of the roller material, and the higher the ratio of M 7C3 type carbide, the better the hardenability, the Cr content needs to be controlled to obtain M 7C3 type carbide in the matrix, and experimental researches show that the Cr content is more than 1.5wt% and exists in the form of M 7C3 carbide, but as the Cr content increases, the eutectic point moves leftwards, and the C content and the Cr content need to be comprehensively considered, so that the Cr element exists in the form of carbide, and less Cr element exists in the matrix in the form of solid solution. This is because the rolled high alloy wire rod often contains a large amount of Cr due to the special property of the wire rod, and the steel sticking phenomenon often occurs when the Cr content of the solid solution in the roller matrix is too high, and a large number of experiments show that the steel sticking phenomenon occurs when the Cr content in the roller exceeds 3.0wt%, so that the mass percentage of Cr is controlled to be 1.5wt% < Cr <3.0wt%.
Ni (nickel) can refine matrix and strengthen hardening performance of steel, and experiments show that the addition of Ni in the matrix of roller has obvious effect of improving toughness and heat strength of steel. However, considering that Ni is a rare element, the addition amount is controlled to be only between 0.8 and 1.5%, when the mass content of Ni is less than 0.8%, the increase of the normal-temperature toughness and the heat strength of the roller is not obvious, when the mass content of Ni is between 0.8 and 1.5%, the increase of the normal-temperature toughness and the heat strength of the roller is increased along with the increase of the Ni content, and when the mass content of Ni is more than 1.5%, the increase of the normal-temperature toughness and the heat strength is not consistent with the increase of the cost, namely the cost performance is not high.
V (vanadium) in the research range of the test of the invention, with the increase of the V addition amount, the bainitic structure is obviously thinned, the hardness and the transformation amount of the bainitic ductile iron are both increased, and the micro hardness of the austenite and the bainitic structure is not greatly changed. Experimental study shows that the optimal range of V content is 1.5-3.2wt%.
The mechanism of action of V refining the bainitic structure can be categorized into two aspects. Firstly, V is one of the elements of strengthening ferrite and austenite, and is dissolved into austenite to form solid solution, so that the diffusion speed of carbon is reduced, and the diffusion time is also required, thereby delaying the transformation of austenite and prolonging the transformation period of bainite. Under the continuous cooling conditions of this test, this means that the bainitic transformation will be carried out at a lower temperature. An increase in transformation supercooling will give a greater driving force for bainitic nucleation. In the austenitizing process, VC (vanadium carbon) particles formed in the solidification process have a pinning effect, prevent grain boundary movement and grain growth, refine austenite grains, and provide more favorable nucleation positions for bainite. Due to the effects of the two aspects, the bainitic core is greatly increased, the bainitic structure is refined, and the bainitic transformation amount is increased.
Mo (molybdenum) and W (tungsten) in the technical scheme of the invention, mo is taken as a strong carbide forming element, so that the stability of austenite and the hardenability of a roller matrix are improved, the tempering brittleness of the second type is prevented, and M 6 C-type carbide formed by Mo and W is adopted, so that the stability of MC-type carbide and the tempering resistance stability of the matrix are improved, and the generation of hot cracks is inhibited;
Nb (niobium) has strong affinity with carbon, nitrogen and oxygen, can form extremely stable compound, has the functions of refining grains, improving the coarsening temperature of the grains, hardenability and tempering stability, and can improve the wear resistance of a thickening die by taking Nb as a hard element, so that the mass percentage of the Nb element is controlled to be 0.12-0.25wt%.
The invention provides a heat treatment process of an anti-stripping roller material of a high-line pre-finishing mill group, which comprises the following steps of annealing and quenching tempering.
Preferably, the annealing step comprises the steps of cooling the cast roller material to 930-950 ℃, namely carrying out furnace-following heat preservation annealing treatment for 3-4 hours, stopping heating, gradually cooling to 600 ℃, discharging, and air cooling to room temperature.
Preferably, the quenching and tempering step includes:
s1, heating and preserving heat for the first time;
s2, heating and preserving heat for the second time;
s3, heating and preserving heat for the third time;
S4, spray quenching;
S5, tempering at high temperature.
Preferably, the first temperature rise and heat preservation comprises heating the roller material treated in the annealing step at a temperature rise speed of 180-200 ℃ per hour, and carrying out temperature equalization and heat preservation for 10-12min at 700 ℃.
Preferably, the second temperature rise and heat preservation comprises the following steps of continuously rising the temperature at the temperature rise speed of 180-200 ℃ per hour on the basis of the step S1, and carrying out the temperature equalization and heat preservation for 10-12min at the temperature of 900 ℃.
Preferably, the third heating and heat preservation comprises the step of heating to 980-1100 ℃ based on the step S2, heat preservation for 30-40min, and discharging and quenching.
Preferably, the spray quenching comprises the step S3 of testing the spray flow of a spray cooling device to ensure that the cooling speed of the roll body of the roll material is 2-4 ℃ per second, and after 245-550 seconds, blowing the roll body to the maximum return temperature of 340-350 ℃ in the blowing stage until the roll temperature is 150-170 ℃, stopping blowing and air-cooling until the roll body temperature is stable at 150-170 ℃.
Preferably, the high-temperature tempering step comprises the steps of preheating a tempering furnace to 100-150 ℃, heating a roller material at a temperature rising speed of 180-200 ℃ per hour on the basis of the step S4, tempering and preserving heat at 480-600 ℃ for 90-120min, cooling to 150 ℃ along with the furnace, discharging, air cooling to room temperature, and repeating the high-temperature tempering process for 2-3 times.
In the treatment process steps, multiple temperature-equalizing heat preservation is carried out in the heating process, and is characterized in that the heating speed is high, when the quenching temperature is high, the roller can be heated uniformly by short-time temperature-equalizing heat preservation, and therefore, in the steps S1 and S2, the temperature-equalizing heat preservation is carried out twice for 10-12min at 700 ℃ and 900 ℃.
In the steps S3 and S4 of the treatment process, high-temperature quenching is carried out at 980-1100 ℃, the spray flow is reasonably controlled, the cooling speed of the roller body is controlled to be 2-4 ℃ per second, and the microstructure is controlled to be bainite, a small amount of martensite, residual austenite and carbide. The spray cooling time is controlled to be 245-550s, and the thickness of the working layer is properly controlled to be 35-40mm.
The high temperature quenching is performed at 980-1100C because the alloy composition in the roll material is optimized in the present patent, wherein the high melting point carbide is increased. MC is carbide of V, precipitates during eutectic transformation or precipitates from austenite, the initial solid solution temperature is 1000-1150 ℃, and VC particles are fine and uniformly distributed. M 6 C is carbide of W and Mo, is dissolved in austenite at 1050-1300 ℃, M 6 C is quite stable, is not easy to gather and grow up, and can increase the hardness and wear resistance of the die. M 7C3 is Cr carbide, which is a primary eutectic carbide or a secondary carbide precipitated from austenite, and can be dissolved into elements such as W, mo, V and the like, so that the wear resistance is improved, and the friction coefficient is reduced. M 7C3 is dissolved in austenite at 950-1150 ℃, M 23C6 is another carbide of Cr, and the solution is started at 1000-1020 ℃ and is completely dissolved in austenite at 1150-1200 ℃. Therefore, higher quenching temperatures of 980-1100 ℃ must be used to adequately dissolve the carbide into the matrix.
In the high-temperature tempering step of the treatment process S5, the quenching process adopts high-temperature quenching. Experiments show that the high-temperature quenching is adopted, and the tempering temperature of 480-600 ℃ is matched, so that the thermal fatigue resistance of the roller iron roller is increased, the thermal cracking initiation time of the roller surface is delayed, and the crack propagation speed is also reduced in the service process, because the austenitizing temperature is increased, more carbide is melted in a matrix, the matrix alloy element and the carbon solid solubility are increased, the matrix is effectively reinforced, the toughness is improved, and the tempering resistance of the roller body is improved, the thermal cycling stability is also improved, and failures such as roller surface flaking and the like in the rolling process are effectively reduced due to the higher tempering temperature. The tempering heat preservation time is controlled within 120min, so that the hardness of the stretch reducing roller meets the requirement, and the stretch reducing roller has higher strength and toughness.
Advantageous effects
Compared with the traditional pearlite material roller, the roller material disclosed by the invention has the advantages that the excessive steel amount is improved by 1.5 times, the roller surface of the lower machine is free from peeling and microcrack, and the grinding amount is reduced by 20-30%. The comprehensive cost performance is improved by more than 2 times.
The new material and the heat treatment process of the high-speed wire pre-finishing mill group roller newly designed in the invention increase the toughness of the roller matrix by designing the material components so as to meet the low-temperature rolling requirements of high-strength steel such as spring steel, cold heading steel and the like.
The invention adopts a matched heat treatment process, so that the normal temperature and high temperature mechanical properties of the new roller material are comprehensively improved, especially the high temperature toughness, oxidation resistance and thermal crack resistance are greatly improved, the problems of short service life, peeling frequently occurring and the like of a single machine are solved, the production efficiency is improved, the production cost is reduced, and meanwhile, the microstructure of the roller treated by the heat treatment step is improved from original pearlite to bainite, so that the accident resistance of the roller material matrix is further improved.
The high-speed wire pre-finishing mill group roller developed by the invention has the hardness of 75-80HSD at normal temperature, the tensile strength of 600-650MPa, the hardness of 50-55HSD at 600 ℃, the tensile strength of 500-550MPa and excellent service performance.
The bainite ductile iron roller special for rough rolling is developed, the special alloy elements are added to strengthen and refine the matrix structure, the chemical components and the heat treatment process are designed and optimized, and the bainite+martensite type roller material is developed on the premise of not greatly increasing the cost, so that the roller has higher matrix strength, and the accident resistance, the wear resistance and the single-time service life of the roller of the rough mill stand are improved.
Drawings
FIG. 1 is a graph showing the crystal phase of the roll of example 1 after the heat treatment step (scale: 20 μm).
Detailed Description
Example 1
The first aspect of the example provides an anti-stripping roll material of a high-speed finish rolling unit, wherein the roll material comprises the following chemical element components in percentage by mass of 2.6% of C, 1.3% of Si, 0.5% of Mn, 1.5% of Cr, 1.0% of Ni, 0.2% of Mo, 1.5% of V, 0.5% of W, 0.12% of Nb, the balance of Fe and unavoidable impurities.
In a second aspect, the present invention provides a process for heat treating high-line pre-finishing mill train spalling-resistant roll material, comprising the steps of annealing and quench tempering.
The annealing step comprises the steps of cooling the cast roller material to 940 ℃, namely carrying out furnace-following heat preservation annealing treatment for 4 hours, stopping heating, slowly cooling to 600 ℃ along with the furnace, and discharging and air cooling to 25 ℃ at room temperature.
The quenching and tempering steps comprise:
S1, heating the roller material treated in the annealing step at a heating rate of 200 ℃ per hour, and carrying out uniform temperature preservation for 10min at 700 ℃;
s2, heating and preserving heat for the second time, namely continuously heating at the heating speed of 200 ℃ per hour on the basis of the step S1, and carrying out uniform temperature preservation for 10 minutes when the temperature is raised to 900 ℃;
s3, heating and preserving heat for the third time, namely heating to 1100 ℃ on the basis of the step S2, preserving heat for 40min, and discharging and quenching;
S4, spray quenching, namely on the basis of the step S3, enabling the cooling speed of the roll body of the roll material to be 2 ℃ per second through the spray flow of the test spray cooling device, blowing 475S to the roll body, wherein the highest return temperature is 350 ℃ in the blowing stage, the roll temperature is 150 ℃, stopping blowing and air cooling until the roll body temperature is stabilized at 150 ℃;
s5, high-temperature tempering, namely preheating a tempering furnace to 150 ℃, heating a roller material to 600 ℃ at a temperature rising speed of 180 ℃ per hour on the basis of the step S4, tempering and preserving heat for 120min, cooling to 150 ℃ along with the furnace, discharging, and air cooling to room temperature of 25 ℃.
The high temperature tempering step is repeated 3 times.
Example 1 the crystalline phase diagram of the material after the roll was subjected to the heat treatment step is shown in figure 1.
Examples 2 to 5
The embodiments of examples 2-5 are identical to example 1, except that the roll material has different mass percentages of the chemical element components, as detailed in Table 1.
TABLE 1 Components (wt%) of examples 1-5
Comparative example 1
The first aspect of the present example provides a roll material, wherein the roll material comprises, by mass, 2.8% of C, 0.7% of Si, 0.6% of Mn, 1.6% of Cr, 1.0% of Ni, 0.2% of Mo, 1.5% of V, and the balance of Fe and unavoidable impurities.
In a second aspect, the present invention provides a process for heat treating roll material, comprising the steps of softening and annealing a cast roll at 1000 ℃, quenching at 960 ℃, tempering at 500 ℃, and cooling to room temperature of 25 ℃.
Performance testing
1. Mechanical property test
Test objects are normal temperature (25 ℃) mechanical properties and high temperature mechanical properties (test temperature: 600 ℃) of the roller materials in the examples 1-5, wherein the normal temperature mechanical properties are referred to as GB/T228.1-2021, the high temperature mechanical properties are referred to as GB/T228.2-2015, and the test results are shown in Table 2.
Table 2 mechanical properties test results table
As shown in tables 1 and 2, the rolling stand rolls in the new materials of examples 1 to 5 have a tensile strength R m of 600 to 650MPa, an impact energy A KU2 of 3.6 to 5.0J, a hardness HSD of 52 to 55, a tensile strength of 510 to 548MPa and a hardness HSD of 51 to 55 at room temperature.
2. Mechanical property test
Test objects the rolls described in example 1 and comparative example 1, the test results are detailed in table 3.
Table 3 comparison table of average rolling amount on single pass
The method for testing the average rolling quantity of a single machine or the testing standard is that a conventional roller has a rolling regulation for regulating the fixed rolling tonnage according to the use experience, and the roller is replaced when the rolling tonnage is reached.
After the new material roller is started, the working personnel can get to the side of the rolling mill and observe the condition of the roller surface after the short stop time for switching the specification, if the defects such as microcracks, flaking and the like are not observed, the new material roller can be continuously used until the defect of the roller surface appears and is started, and the rolling tonnage is counted at the moment, so that the single starting rolling tonnage of the new material roller is obtained.
Aiming at the problems that the roll surface of the existing roll is easy to peel and the single machine-on time cannot meet the production line requirement, the novel material high-performance roll material prepared by adopting the novel material and the heat treatment process thereof has excellent toughness, wear resistance and heat cracking resistance, solves the problems of short service life, frequent peeling and the like of the raw material roll, improves the production efficiency, reduces the production cost and has better popularization and application prospect.
Claims (8)
1. The high-speed wire pre-finishing mill group anti-stripping roll material is characterized by comprising, by mass, 2.6-3.6% of C, 1.3-2.0% of Si, 0.5-0.8% of Mn, 1.5-3.0% of Cr, 1.0-2.5% of Ni, 0.2-0.8% of Mo, 1.5-3.2% of V, 0.5-1.0% of W, 0.12-0.25% of Nb, the balance of Fe and unavoidable impurities, wherein the mass percentage of V, mo and W satisfies V+Mo+W/2=1.9-4.5%.
2. A heat treatment process for the anti-spalling roll material of the high-line pre-finishing mill group according to claim 1, wherein the heat treatment process for the roll material comprises an annealing step and a quenching and tempering step;
The quenching and tempering steps comprise:
s1, heating and preserving heat for the first time;
s2, heating and preserving heat for the second time;
s3, heating and preserving heat for the third time;
S4, spray quenching;
S5, tempering at high temperature.
3. The process for heat treating high-line pre-finishing mill train spalling-preventing roll material of claim 2, wherein said annealing step comprises:
And (3) cooling the cast roller material to 930-950 ℃, namely carrying out furnace-following heat preservation annealing treatment for 3-4 hours, stopping heating, slowly cooling to 600 ℃ along with the furnace, and discharging and air cooling to room temperature.
4. The process for heat treatment of high-line pre-finishing mill group anti-spalling roll material according to claim 2, wherein said first temperature rise and heat preservation comprises:
heating the roller material treated in the annealing step at a heating rate of 180-200 ℃ per hour, and carrying out uniform temperature insulation for 10-12min at 700 ℃.
5. The process for heat treatment of high-speed wire pre-finishing mill group anti-spalling roll material according to claim 2, wherein said second heating and heat preservation comprises:
And (S1) continuously heating the roller material at a heating rate of 180-200 ℃ per hour on the basis of the step S1, and carrying out uniform temperature insulation for 10-12min at 900 ℃.
6. The process for heat treatment of high-speed wire pre-finishing mill group anti-spalling roll material according to claim 2, wherein said third heating and heat preservation comprises:
and S2, on the basis of the step S, heating the roller material to 980-1100 ℃, preserving heat for 30-40min, and discharging and quenching.
7. The process for heat treatment of high-line pre-finishing mill train spalling-preventing roll material of claim 2, wherein said spray quenching comprises:
And S3, on the basis of the step S3, the cooling speed of the roll body of the roll material is 2-4 ℃ per second through the spray flow of the spray cooling device, after 245-550 seconds, blowing is carried out on the roll body, the highest return temperature in the blowing stage is 340-350 ℃, the roll temperature is 150-170 ℃, and the blowing is stopped and the air cooling is carried out until the roll body temperature is stable at 150-170 ℃.
8. The heat treatment process for high-line pre-finishing mill train spalling-preventing roll material according to claim 2, wherein the high-temperature tempering step in step S5 comprises:
Preheating a tempering furnace to 100-150 ℃, heating a roller material in the tempering furnace at a temperature rising speed of 180-200 ℃ per hour on the basis of the step S4, rising to 480-600 ℃, tempering and preserving heat for 90-120min, cooling to 150 ℃ along with the furnace, discharging, air cooling to room temperature, and repeating the high-temperature tempering step for 2-3 times.
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| US6916444B1 (en) * | 2002-02-12 | 2005-07-12 | Alloy Technology Solutions, Inc. | Wear resistant alloy containing residual austenite for valve seat insert |
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