CN105648161A - Preheat treatment method for large-size forged steel supporting roller - Google Patents
Preheat treatment method for large-size forged steel supporting roller Download PDFInfo
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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
- C21D1/28—Normalising
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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
- C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
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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
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
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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
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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
- 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
- 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
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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
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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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
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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
- C21D2211/009—Pearlite
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Abstract
The invention discloses a preheat treatment method for a large-size forged steel supporting roller. The after-forging heat treatment process is technically characterized in that high-temperature normalizing and high-temperature tempering processes are adopted under the normalizing heating temperature of 800 to 970 DEG C and the heating rate of less than 90 DEG C/h; after the temperature is averaged, the heat insulation time is determined according to the diameter of a roller body of the supporting roller; the heat insulation time for the supporting roller with the diameter of Phi 1,000-1,700 mm is 10 to 40 hours; after the roller is cooled in air, high-temperature tempering is carried out under the tempering temperature of 500 to 750 DEG C and the heating rate of less than 60 DEG C/h; after the temperature is averaged, the heat insulation time is 40 to 90 hours. A hardening and tempering process is as follows: an oil quenching and high-temperature tempering process is adopted; the preheat temperature for the supporting roller is 550 to 700 DEG C and is insulated for 5 to 20 hours; then the supporting roller is heated to the quenching temperature of 800 to 970 DEG C under the heating rate of 80 DEG C/h; after the heat is insulated for certain time, oil quenching is carried out for cooling time of 100 to 400 min; once oil is discharged, tempering is carried out immediately under the tempering temperature of 500 to 750 DEG C and the heating rate of less than 50 DEG C/h; after being averaged, the temperature is insulated for 20 to 90 hours.
Description
Technical field
The present invention relates to a kind of large forged back-up roll conditioning treatment method, belong to heavy forging technical field of heat treatment technology.
Background technology
Large forged back-up roll is the important core parts of strip-mill strip, plays the effect supported with steady operation roller, owing to it works for a long time at high loads, has higher mechanical property requirements: working lining high-wearing feature, fatigue resistance, uniformity of hardness; Heart portion then requires have good obdurability. Continuous increase along with modern steel rolling demand, the dimensions of support roll is consequently increased, some diameter reaches one and half even more than two meters, but the problem of the brittle fracture of backing roll and premature failure also becomes increasingly conspicuous, and improper owing to producing, large scale backing roll repeatedly occurs roll breakage in production and processing, placement or use procedure or puts the accident split.
Traditional backing roll Technology for Heating Processing mainly includes heat treatment after forging and Tempering and Quenching before differential temperature heat treatment. The effect of heat treatment after forging is mainly crystal grain thinning, adjust tissue and uniformity, dehydrogenation prevent white point from being formed, being conducive to machining, main technique includes high temperature normalizing+spheroidizing+high-temperature tempering process, high temperature normalizing+cryogenic normalizing+spheroidizing+high tempering (such as patent CN1024717965A) or full annealing+spheroidizing+normalizing+tempering (such as patent CN103088199A) etc. simultaneously; Tempering and Quenching mainly makes the hardness of backing roll roll neck reach requirement and make heart portion obtain spheroidizing pearlite, having good impact flexibility, thus improving the break resistance of backing roll, being generally adopted normalizing air cooling or oil quenchinng and tempering. The main material of Mill conventional at present is 50Cr3MoV, 70Cr3NiMo, 45Cr4NiMoV, 50Cr5NiMoV etc., increasing however as alloying element, the kind of carbide in unlike material, solution temperature gap are big, and to obtain the tissue distribution that supporting roll centre portion is excellent, it is bigger that process of thermal treatment formulates difficulty.
Current backing roll conditioning treatment technique also exists weak point: in heat treatment after forging spheroidizing in order that reduce hardness, improve cutting ability, for modifier treatment obtain spheroidizing pearlite prepare; And the hardening heat scope of modifier treatment is excessively wide in range, refining temperature is too high and long-time heat preservation, being easily caused heart portion carbide all to dissolve, austenite composition is relatively uniform, is close to balance change and forms sheet pearlite in cooling procedure, after forging, the spheroidising of state acts on after modified high temperature quenches and being eliminated, not up to spheroidizing, and technique is tediously long, takes time and effort, and cause that impact flexibility sharply declines, increase the risk of backing roll fracture.
Summary of the invention
In order to overcome the above-mentioned technologic deficiency of backing roll conditioning treatment, it is an object of the invention to provide after the forging of a kind of large forged back-up roll and Tempering and Quenching method, the hardening heat of unlike material backing roll is combined with carbide content, realize Technology for Heating Processing accurately to control, thus shortened process, reduce manufacturing cost, and guarantee tissue and the performance of supporting roll centre portion excellence.
The technical solution adopted for the present invention to solve the technical problems is: a kind of large forged back-up roll conditioning treatment method, the steps include:
One, heat treatment after forging process: adopt high temperature normalizing and high-temperature tempering process, normalizing heating-up temperature is 800-970 DEG C, heating rate is less than 90 DEG C/h, after samming, temperature retention time is determined depending on the size of backing roll barrel diameter, described samming reaches holding temperature with each portion faces homogeneous temperature of backing roll in stove and is as the criterion, diameter is the backing roll temperature retention time of �� 1000-1700mm is 10-40 hour, high tempering is carried out after air cooling, temperature is 500-750 DEG C, heating rate is less than 60 DEG C/h, and after samming, temperature retention time is 40-90 hour.
Two, modifier treatment process: adopt oil quenching and high-temperature tempering process, backing roll preheating temperature is 550-700 DEG C, temperature retention time 5-20 hour, it is then heated to hardening heat 800-970 DEG C, heating rate is less than 80 DEG C/h, carrying out oil quenching after held for some time, cool time is 100-400min; Fuel-displaced tempering at once, temperature is 500-750 DEG C, and heating rate is less than 50 DEG C/h, and after samming, temperature retention time is 20-90h.
The invention has the beneficial effects as follows:
(1) heat treatment after forging is at minimizing spheriodization process thereof compared with traditional handicraft, suitably heighten temperature, both met its crystal grain thinning, elimination segregation adjustment tissue and dehydrogenation and prevented the requirements such as white point formation, and having reduced again operation, reducing energy consumption thus saving cost.
(2) modifier treatment is strictly determined the hardening heat scope of concrete alloy material and shortens temperature retention time, control undissolved carbide content, ensure that the pearlitic spheroidization degree in unlike material supporting roll centre portion is high, thus the toughness of backing roll and anti-accident performance are greatly improved.
Accompanying drawing explanation
45Cr4NiMoV material carbide dissolution figure in Fig. 1 embodiment of the present invention 1 technique.
Fig. 2 present invention compares 45Cr4NiMoV material carbide dissolution figure in technique 1.
The modified rear pearlitic spheroidization degree figure of 45Cr4NiMoV in Fig. 3 embodiment of the present invention 1 technique.
Fig. 4 present invention compares the modified rear pearlitic spheroidization degree figure of 45Cr4NiMoV in technique 1.
50Cr5NiMoV material carbide dissolution figure in Fig. 5 embodiment of the present invention 2 technique.
Fig. 6 present invention compares 50Cr5NiMoV material carbide dissolution figure in technique 2.
Fig. 7 present invention compares 50Cr5NiMoV material carbide dissolution figure in technique 3.
The modified rear pearlitic spheroidization degree figure of 50Cr5NiMoV in Fig. 8 embodiment of the present invention 2 technique.
Fig. 9 present invention compares the modified rear pearlitic spheroidization degree figure of 50Cr5NiMoV in technique 2.
Figure 10 present invention compares the modified rear pearlitic spheroidization degree figure of 50Cr5NiMoV in technique 3.
Detailed description of the invention
A kind of large forged back-up roll conditioning treatment method, the steps include:
One, heat treatment after forging process: adopt high temperature normalizing and high-temperature tempering process, normalizing heating-up temperature is 800-970 DEG C, heating rate is less than 90 DEG C/h, after samming, temperature retention time is determined depending on the size of backing roll barrel diameter, described samming reaches holding temperature with each portion faces homogeneous temperature of backing roll in stove and is as the criterion, diameter is the backing roll temperature retention time of �� 1000-1700mm is 10-40 hour, high tempering is carried out after air cooling, temperature is 500-750 DEG C, heating rate is less than 60 DEG C/h, and after samming, temperature retention time is 40-90 hour.
Two, modifier treatment process: adopt oil quenching and high-temperature tempering process, backing roll preheating temperature is 550-700 DEG C, temperature retention time 5-20 hour, it is then heated to hardening heat 800-970 DEG C, heating rate is less than 80 DEG C/h, carrying out oil quenching after held for some time, cool time is 100-400min; Fuel-displaced tempering at once, temperature is 500-750 DEG C, and heating rate is less than 50 DEG C/h, and after samming, temperature retention time is 20-90h.
The method wherein accurately determining unlike material hardening heat scope and temperature retention time, namely hardening heat should select suitable temperature, and supporting roll centre portion undissolved carbide volume content is more than 5% at such a temperature; Temperature retention time is be incubated 1-15 hour after backing roll entirety samming. Utilize the means that carbide extracts and XRD combines, adopt image quantitative statistics principle to calculate the volume content of undissolved carbide simultaneously. Content according to unlike material undissolved carbide determines hardening heat and temperature retention time, thus ensureing the performance that supporting roll centre portion is excellent.
Heavy Back-Up Roll forging ' s block dimension is relatively big, and heart portion regional part and microstructure segregation are serious, and coarse grains, and structural homogenity is poor, thus causing that the whole thermal cycle is long, quality is unstable. Top layer austenitizing is only carried out during due to backing roll finished heat treatment and differential quenching, region, heart portion is only equivalent to carry out short time high temperature temper in the process, the final tissue supporting roll centre portion and performance state still depend primarily on conditioning treatment, thus directly affecting the toughness and tenacity of backing roll.
Heat treatment after forging process high-temperature normalizing+high tempering that the present invention adopts, effectively reduces segregation and reticular tissue, crystal grain thinning, and dehydrogenation effect is notable and is conducive to cutting, implements ready smoothly for modifier treatment. The shortening of rationally selection and the temperature retention time of hardening heat in modified process, make undissolved carbide content more than 5%, roll centre portion rate of cooling is supported slower during quenching, thus the pearlitic spheroidization degree obtained is high, and ensure the obdurability in supporting roll centre portion, simultaneously by adjusting temperature and time, roll neck hardness can be made to meet requirement.
Embodiment 1
The embodiment of the present invention 1 backing roll material 45Cr4NiMoV, its chemical composition and dispensing are with weight (%), for C:0.4-0.5; Si:0.4-1.0; Mn:0.4-1.0; Cr:3.5-4.5; Mo:0.4-0.8; Ni:0.4-0.8; V:0.05-0.25; All the other are Fe and other impurity. Backing roll is of a size of �� 1410mm(barrel diameter) �� 2815mm(barrel length) �� 5660mm(total length).
One, heat treatment after forging process: normalizing temperature is 880-920 DEG C, heating rate is less than 90 DEG C/h, and the temperature retention time after samming is 10-25 hour, high tempering is carried out after air cooling, temperature is 500-700 DEG C, and heating rate is less than 60 DEG C/h, and after samming, temperature retention time is 50-90 hour.
Two, hardening and tempering method: backing roll preheating temperature is 550-700 DEG C, temperature retention time 5-20 hour, is then heated to hardening heat 880 �� 20 DEG C, heating rate, less than 80 DEG C/h, carries out oil quenching after insulation 5h, and cool time is about 300 �� 50min; Fuel-displaced tempering at once, temperature is 550-650 DEG C, and heating rate is less than 50 DEG C/h, and after samming, temperature retention time is 10-40h. Utilize the means that carbide extracts and XRD combines, adopt image quantitative statistics principle to calculate the volume content of undissolved carbide simultaneously. When under this technique, undissolved carbide volume content is 5.85%, the modified rear heart portion impact flexibility A that 45Cr4NiMoV material backing roll of the present invention obtainsku2For 62J, excellent performance.
Carrying out identical heat treatment after forging as reference examples, change hardening heat 920 DEG C (�� 20 DEG C) in modifier treatment, holding time is to 20h, and other compositions and heat treatment mode are identical with embodiment. Fig. 1 is the embodiment of the present invention 1 technique, Fig. 2 is 45Cr4NiMoV material carbide dissolution situation in comparative example, and Fig. 3 is embodiment 1 technique, Fig. 4 is the modified rear pearlitic spheroidization degree of 45Cr4NiMoV in comparative example. Along with the rising of hardening heat, undissolved carbide content gradually decreases, and after modifier treatment, pearlite is sheet, M23C6Carbide increases, near-spherical M7C3Reducing, nodularization degree is gradually lowered, thus being substantially reduced the plasticity and toughness of material. The two undissolved carbide content and mechanical property comparative result are as shown in table 1, table 1 finding conditioning treatment of the present invention technique make supporting roll centre portion have better impact flexibility, thus improving the anti-accident performance of backing roll.
Embodiment 2
The embodiment of the present invention 2 backing roll material 50Cr5NiMoV, its chemical composition and dispensing, with weight (%), comprise: C:0.4-0.6; Si:0.4-1.0; Mn:0.4-1.0; Cr:4.5-5.5; Mo:0.4-0.8; Ni:0.4-0.8; V:0.05-0.3; All the other are Fe and other impurity. Backing roll is of a size of �� 1340mm(barrel diameter) �� 1380mm(barrel length) �� 4870mm(total length).
Following technique is adopted to carry out heat treatment embodiment steel: after forging, first blank carries out heat treatment after forging, normalizing temperature is 900-940 DEG C, heating rate is less than 90 DEG C/h, temperature retention time after samming is 10-25 hour, high tempering is carried out after air cooling, temperature is 550-700 DEG C, and heating rate is less than 60 DEG C/h, and after samming, temperature retention time is 50-90 hour.
Next carries out modifier treatment, and preheating temperature is 580-700 DEG C, temperature retention time 5-20 hour, is then heated to hardening heat 900 �� 20 DEG C, and heating rate, less than 80 DEG C/h, carries out oil quenching after insulation 5h, and cool time is about 300 �� 50min; Fuel-displaced tempering at once, temperature is 550-650 DEG C, and heating rate is less than 50 DEG C/h, and after samming, temperature retention time is 10-40h. Also with the quantitative statistics method of undissolved carbide, the means that namely carbide extracts and XRD combines, adopt image quantitative statistics principle to calculate the volume content of undissolved carbide under different process simultaneously. When backing roll 50Cr5NiMoV material undissolved carbide content in the present embodiment is 8.67%, it is thus achieved that modified rear support roll centre portion pearlitic spheroidization degree is higher, and impact flexibility Aku2Up to 83J.
Changing hardening heat 940 DEG C �� 20 DEG C as reference examples, temperature retention time 15h, other compositions and heat treatment mode are identical with embodiment, record its ballistic work and all significantly reduce. Fig. 5 is the embodiment of the present invention 2 technique, Fig. 6 and Fig. 7 is 50Cr5NiMoV material carbide dissolution situation in comparative example, and Fig. 8 is embodiment 2 technique, Fig. 9 and Figure 10 is the modified rear pearlitic spheroidization degree of 50Cr5NiMoV in comparative example. Along with hardening heat reduces, carbide dissolution degree reduces, and after modifier treatment, pearlitic spheroidization degree improves, thus improving plasticity and toughness. Table 2 compares for the two undissolved carbide content and mechanical property, when visible hardening and tempering process of the present invention and undissolved carbide volume content are more than 5%, the impact flexibility in supporting roll centre portion is all higher, reducing hardening heat simultaneously and shorten temperature retention time, effectively reducing energy consumption thus reducing production and time cost.
Claims (3)
1. a large forged back-up roll conditioning treatment method, is characterized in that: the steps include:
One, heat treatment after forging process: adopt high temperature normalizing and high-temperature tempering process, normalizing heating-up temperature is 800-970 DEG C, heating rate is less than 90 DEG C/h, after samming, temperature retention time is determined depending on the size of backing roll barrel diameter, described samming reaches holding temperature with each portion faces homogeneous temperature of backing roll in stove and is as the criterion, diameter is the backing roll temperature retention time of �� 1000-1700mm is 10-40 hour, high tempering is carried out after air cooling, temperature is 500-750 DEG C, heating rate is less than 60 DEG C/h, and after samming, temperature retention time is 40-90 hour;
Two, modifier treatment process: adopt oil quenching and high-temperature tempering process, backing roll preheating temperature is 550-700 DEG C, temperature retention time 5-20 hour, it is then heated to hardening heat 800-970 DEG C, heating rate is less than 80 DEG C/h, carrying out oil quenching after held for some time, cool time is 100-400min; Fuel-displaced tempering at once, temperature is 500-750 DEG C, and heating rate is less than 50 DEG C/h, and after samming, temperature retention time is 20-90h.
2. a kind of large forged back-up roll conditioning treatment method according to claim 1, is characterized in that: backing roll material 45Cr4NiMoV, and its chemical composition and dispensing are with weight (%), for C:0.4-0.5; Si:0.4-1.0; Mn:0.4-1.0; Cr:3.5-4.5; Mo:0.4-0.8; Ni:0.4-0.8; V:0.05-0.25; All the other are Fe and other impurity; Backing roll is of a size of �� 1410mm(barrel diameter) �� 2815mm(barrel length) �� 5660mm(total length);
One, heat treatment after forging process: normalizing temperature is 880-920 DEG C, heating rate is less than 90 DEG C/h, and the temperature retention time after samming is 10-25 hour, high tempering is carried out after air cooling, temperature is 500-700 DEG C, and heating rate is less than 60 DEG C/h, and after samming, temperature retention time is 50-90 hour;
Two, hardening and tempering method: backing roll preheating temperature is 550-700 DEG C, temperature retention time 5-20 hour, is then heated to hardening heat 880 �� 20 DEG C, heating rate, less than 80 DEG C/h, carries out oil quenching after insulation 5h, and cool time is about 300 �� 50min; Fuel-displaced tempering at once, temperature is 550-650 DEG C, and heating rate is less than 50 DEG C/h, and after samming, temperature retention time is 10-40h.
3. a kind of large forged back-up roll conditioning treatment method according to claim 1, is characterized in that: backing roll material 50Cr5NiMoV, and its chemical composition and dispensing, with weight (%), comprise: C:0.4-0.6;Si:0.4-1.0; Mn:0.4-1.0; Cr:4.5-5.5; Mo:0.4-0.8; Ni:0.4-0.8; V:0.05-0.3; All the other are Fe and other impurity; Backing roll is of a size of �� 1340mm(barrel diameter) �� 1380mm(barrel length) �� 4870mm(total length);
One, heat treatment after forging process: normalizing temperature is 900-940 DEG C, heating rate is less than 90 DEG C/h, and the temperature retention time after samming is 10-25 hour, high tempering is carried out after air cooling, temperature is 550-700 DEG C, and heating rate is less than 60 DEG C/h, and after samming, temperature retention time is 50-90 hour;
Two, hardening and tempering method: preheating temperature is 580-700 DEG C, temperature retention time 5-20 hour, is then heated to hardening heat 900 �� 20 DEG C, heating rate, less than 80 DEG C/h, carries out oil quenching after insulation 5h, and cool time is about 300 �� 50min; Fuel-displaced tempering at once, temperature is 550-650 DEG C, and heating rate is less than 50 DEG C/h, and after samming, temperature retention time is 10-40h.
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| CN115161549A (en) * | 2022-05-27 | 2022-10-11 | 郑州轻研合金科技有限公司 | High-tensile-strength alloy steel plate and preparation method thereof |
| CN117051333A (en) * | 2023-10-12 | 2023-11-14 | 山西同航特钢有限公司 | Forged steel supporting roller and preparation method thereof |
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| CN106884123A (en) * | 2016-12-29 | 2017-06-23 | 中钢集团邢台机械轧辊有限公司 | Universal mill alloy cast steel material BD rolls and its manufacture method |
| CN106636665B (en) * | 2016-12-29 | 2018-08-21 | 沈阳科金特种材料有限公司 | A kind of preparation method of nuclear power motor axis |
| CN108247284A (en) * | 2017-12-04 | 2018-07-06 | 广东精铟海洋工程股份有限公司 | A kind of manufacturing method of low temperature heavy duty high-performance safe locking pin |
| CN108247284B (en) * | 2017-12-04 | 2019-01-29 | 广东精铟海洋工程股份有限公司 | A kind of manufacturing method of low temperature heavy duty high-performance safe locking pin |
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| CN110551880A (en) * | 2019-10-24 | 2019-12-10 | 成都先进金属材料产业技术研究院有限公司 | softening heat treatment process for small-size 22Si2MnCrNi2MoA steel rolled material |
| CN111676349A (en) * | 2020-05-12 | 2020-09-18 | 江阴兴澄合金材料有限公司 | Tempering process of round steel and application thereof |
| CN111647721A (en) * | 2020-06-18 | 2020-09-11 | 建龙北满特殊钢有限责任公司 | Method for solving low-temperature impact energy of high-alloy structural steel after hardening and tempering |
| CN114672621A (en) * | 2022-03-28 | 2022-06-28 | 河南中原特钢装备制造有限公司 | Heat treatment process for improving 1Cr11MoV calendering roller network structure |
| CN114672621B (en) * | 2022-03-28 | 2023-09-26 | 河南中原特钢装备制造有限公司 | Heat treatment process for improving 1Cr11MoV calendering roller reticular structure |
| CN115161549A (en) * | 2022-05-27 | 2022-10-11 | 郑州轻研合金科技有限公司 | High-tensile-strength alloy steel plate and preparation method thereof |
| CN117051333A (en) * | 2023-10-12 | 2023-11-14 | 山西同航特钢有限公司 | Forged steel supporting roller and preparation method thereof |
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