CN108220815A - Hot forging high heat-intensity, high impact toughness hot die steel and preparation method - Google Patents

Hot forging high heat-intensity, high impact toughness hot die steel and preparation method Download PDF

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CN108220815A
CN108220815A CN201711377222.5A CN201711377222A CN108220815A CN 108220815 A CN108220815 A CN 108220815A CN 201711377222 A CN201711377222 A CN 201711377222A CN 108220815 A CN108220815 A CN 108220815A
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steel
forging
hot
intensity
heat
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CN108220815B (en
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周健
马党参
迟宏宵
林鹏
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Central Iron and Steel Research Institute
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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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
    • B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
    • 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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
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Abstract

A kind of hot forging high heat-intensity, high impact toughness hot die steel and preparation method, belong to technical field of mold steel.Mould steel chemical component weight % is matched：C:0.40~0.50%, Si:0.30~0.60%, S≤0.006%, P≤0.01%, Mn:0.60~0.9%, Mo:1.80~2.80%, Cr:3.00~3.80%, V:0.40~0.60%, Ni:0.80~1.40, Al:0.3~0.6, Co:0.50~1.10%, rare earth element:0.002~0.008%, surplus is Fe and inevitable impurity.The steel is through smelting, ingot casting, and the steel ingot of preparation carries out multiway forging hot-working after High temperature diffusion is heat-treated, and cooling, microstructure homogenization and refinement heat treatment and isothermal annealing processing are controlled after forging.The advantage is that with higher heat resistance, impact flexibility and quenching degree, particularly suitable making requires high heat-intensity and the big section i.e. section thickness of impact flexibility to be more than 400mm hot forged moulds.

Description

Hot forging high heat-intensity, high impact toughness hot die steel and preparation method
Technical field
The invention belongs to technical field of mold steel, more particularly to a kind of hot forging high heat-intensity, high impact toughness Forming Die Have steel and preparation method.Need high heat-intensity, higher high tempering stability, high-hardenability and impact tough suitable for manufacture The big section hot forged mould of property.
Background technology
Hot die steel is the important component of mould steel, wherein, hot work tool steel is for more than recrystallization temperature Solid metallic is molded, and sizable ratio is occupied in hot die steel.At present, nearly all great primary structure member is all logical Hot-forging forming is crossed to be produced, especially in the manufacturing industry such as various fasteners, standard component, automobile engine, aircraft, There is very big dependence to hot-forging forming technique.With high speed, strong load, high-accuracy forging equipment and high-strength tenacity forging It is commonly used, hot-forging die service condition is more severe, while metal stock forging temperature makes usually all at 1000 DEG C or more It obtains hot work tool steel work cavity surface temperature and is up to 600 DEG C, some regions are because of instantaneous impact and the shadow of frictional force in cavity It rings, temperature is up to 700 DEG C or more.Intensity and hardness are insufficient after mold is repeatedly tempered, and cavity are caused to collapse, high temperature wear, heat Fatigue, this is also that hot forged mould most failure modes occurs, accounts for more than the 70% of total failure mode.Therefore, high heat-intensity, High temperature abrasion resistance, high thermal fatigue resistance and temper resistance become an important evidence of hot work tool steel selection and near several The important directions of year hot-forging forming mould steel research and development.
For a long time, domestic hot forged mould user generally using 5CrNiMo, 5CrNiMoV, H13 (4Cr5MoSiV1) and H21 (3Cr2W8V) steel is as preferred steel grade.Wherein, when mold sections thickness is more than 400mm, mold is usually since center portion is tough Property it is insufficient, be also easy to produce whole phenomenon of rupture during being on active service, usual impact flexibility is the power that this series mould material need to consider first Learn performance.Therefore, large and medium-sized hot forged mould (section thickness is more than 400mm) generally uses 5CrNiMo, 5CrNiMoV steel. 5CrNiMo steel is less due to containing alloying element total amount, and impact flexibility has certain advantage, but since quenching degree is insufficient, generally There are high temperature heat resistance deficiency, mold service temperature influences the thermal fatigue resistance, wear-resisting of mold entirety not above 500 DEG C Property, thermal stability, thus the universal service life of majority 5CrNiMo hot forged moulds only has 6000~7000 times, seriously affects The production efficiency and economic benefits of mold user；5CrNiMoV steel hardenabilities and intensity are slightly higher, but still can not meet big section Requirement of the hot-forging die to heat resistance and service life.Middle-size and small-size hot forged mould (section thickness is less than 400mm) omits toughness reguirements Low, current more than 80% generally using H13 steel, although H13 steel, using relatively extensively, service temperature is less than 600 DEG C, still deposits Heat resistance is insufficient the problem of, it still cannot meet the stringent precise forging die of cavity dimension requirement to mould in actual application Has the performance requirement of material.
Invention content
The object of the present invention is to provide a kind of hot forging high heat-intensity, high impact toughness hot die steel and preparation method, Tradition 5CrNiMo, 5CrNiMoV and H13 hot work tool steel can be substituted, may be used on big section hot forged mould, (section thickness is big In 400mm) high heat-intensity, high impact toughness, the hot die steel of high temper resistance and its preparation process.
The technical solution adopted by the present invention is：(1) Si and V content are reduced, reduces primary carbide quantity in material, makes Material has higher toughness；(2) suitably increase carbide former Mo contents, to make up the high temperature that V content reduction is brought Intensity lacks, while also improves the crystal grain rank in quenching process, improves age hardening effect, and nanoscale is precipitated in drawing process Mo2C improves material at high temperature intensity；(3) the high tempering stability of material is improved by reducing Cr contents, according to C, Cr, Co Composition proportion-mechanical property research, under the alloy system for finding+3% chromium of 0.45% carbon, obtain strong, toughness best match Co elements zone of reasonableness, so as to which invention steel be made to obtain higher elevated temperature strength and preferable impact flexibility, and improve invention The anti-oxidant weightless ability of steel；(4) by Ni to the affecting laws of quenching degree and elevated temperature strength, it is determined that best control model It encloses；(5) by adding a small amount of Al, intermetallic compound Ni is formed with the Ni in steel3Al hardening constituents, while a small amount of Al is as refining Nitrogen agent is determined in deoxidation during steel, reduces oxygen content and crystal grain thinning in steel, improves hardening heat；(6) further addition is a small amount of dilute Earth elements (Ce+La) generate rotten and cleaning molten steel effect, change the Al formed due to the addition of Al2O3Nonmetal inclusion And form, granularity and the distribution of carbide.According to the Mo constituent contents of steel of the present invention, control High temperature diffusion temperature and Diffusion time is directly forged into final size after the completion of diffusion, avoids steel ingot and heat again, shorten manufacturing process flow； Further complete the homogenization of tissue using normalizing+spheroidizing, each element mobility scale and subsequent technique ginseng in steel of the present invention Number show that hot die steel of the present invention has higher heat resistance, tempering after Overheating Treatment by a large amount of experimental data Stability, impact flexibility and excellent cool-hot fatigue resistance.
The specific chemical composition (weight %) of steel of the present invention is：Carbon C:0.40~0.50%, silicon Si:0.30~0.60%, Sulphur S≤0.006%, phosphorus P≤0.01%, manganese Mn:0.60~0.9%, molybdenum Mo:1.80~2.80%, chromium Cr:3.00~ 3.80%, vanadium V:0.40~0.60%, nickel:0.80~1.40%, aluminium Al:0.3~0.6%, cobalt Co:0.50~1.10%, Rare earth element (Ce+La):0.002~0.008%, remaining is Fe and inevitable impurity.
Preferably, the mould steel includes by weight percentage：Carbon C:0.40~0.50%, silicon Si:0.30~ 0.60%, sulphur S≤0.003%, phosphorus P≤0.01%, manganese Mn:0.60~0.9%, molybdenum Mo:2.10~2.60%, chromium Cr:3.20 ~3.50%, vanadium V:0.50~0.60%, nickel:0.80~1.20, aluminium Al:0.3~0.5%, cobalt Co:0.50~0.80%, Rare earth element (Ce+La):0.002~0.006%, remaining is Fe and inevitable impurity.
A kind of hot forging high heat-intensity of the present invention, the preparation method of high impact toughness hot die steel, including following Technical process and step：
(1) High temperature diffusion+forging：Steel is made using the smelting of the smelting processes such as electric furnace, electric furnace+electroslag remelting, vacuum induction Ingot, steel ingot are heated to 1200 DEG C~1250 DEG C 10~15h of High temperature diffusion using three sections of preheatings, homogenize ingot composition.Diffusion It is directly cooled to 1140 DEG C~1180 DEG C 2~4h of heat preservation afterwards, 1050~1100 DEG C are opened forging, are processed using multiway forging, total forging It makes than 6~7,900~950 DEG C of final forging temperature, slow cooling to room temperature；
(2) normalizing and annealing process：Forging stock is warming up to 900 DEG C~1000 DEG C with stove, and that is organized after being forged is uniform Change, after keeping the temperature 4h, be air-cooled to 400 DEG C~500 DEG C hot chargings and enter stove, after 840 DEG C~860 DEG C 4~6h of heat preservation, be cooled to 710 ~740 DEG C heat preservation 8~12h be furnace-cooled to less than 500 DEG C come out of the stove it is air-cooled.
The effect of steel each element of the present invention and proportioning are according to as follows, " % " expression " mass percent " in illustrating below：
C：Phosphorus content determines the matrix hardness of hardened steel in steel, and for hot die steel, the carbon part in steel enters Cause solution strengthening in the matrix of steel, another part carbon will be combined into alloy with the carbide former in alloying element Carbide.For hot die steel, this alloy carbide except it is a small amount of it is remaining in addition to, also require it in drawing process Disperse educt generates post-curing phenomenon on quenched martensite matrix, so as to be remained alloy carbide by equally distributed and be returned Fiery martensitic structure determines the performance of hot die steel.When phosphorus content in mould steel is too high, carbide quantity increases therewith Add, improve the elevated temperature strength of steel, hardness and redhardneas, the wearability of steel improves, but toughness and plasticity can reduce, technique Performance depreciation；And when phosphorus content is too low, it is impossible to ensure to form sufficient amount of carbide in steel, solid solution during Quench heating In carbon and alloying element content reduce, reduce the intensity of steel, hardness, thermohardening and wearability.Numerous studies show carbon At 0.40% or so, there is hot die steel content relatively good obdurability to match.For the present invention, to improve the height of steel It warms epistasis as the main purpose, therefore, the carbon content in steel is slightly improved, and control in 0.40-0.50%, additionally by other The increase and decrease of element has the function that improve impact flexibility.
Cr：Chromium forms carbide, and the quenching degree, corrosion resistance, wearability of steel can be improved in hot die steel.Quench heating Shi Ge is dissolved in austenite, is solid-solution in martensite after quenching, can improve the anti-temper softening ability of steel, by matrix during tempering Middle precipitation, generally forms Cr23C6Alloy carbide, as the raising of temperature and the extension of time have the tendency that roughening, from And tempering hardness is reduced, based on the theory, steel of the present invention reduces chromium content 3.00~3.80% on the basis of H13 steel, into One step preferably 3.20~3.50%.
V：Vanadium can reduce the excessively thermo-responsive tendency of steel.A small amount of vanadium can refine crystalline grain of steel, make through appropriate heat treatment When carbide dispersion is precipitated, vanadium can improve the creep rupture strength and creep resistance of steel, and 0.1- is added in low-alloy steel 0.3% vanadium just has obvious effects on.In hot die steel, content of vanadium is excessively high, will increase the formation of primary carbide VC in steel Probability, the toughness that a large amount of presence of primary carbide will significantly affect steel reduce the ability that hot die steel resists big crackle. But when content of vanadium is less than 0.5%, hardening heat accordingly reduces, and tempering post-curing peak hardness reduces about 1HRC or so, Post-curing effect is influenced to a certain extent, and content of vanadium, which reaches 0.5%, can generate enough post-curing effects.H13 Content of vanadium in steel in 0.80-1.2%, in steel of the present invention content of vanadium control 0.40~0.60%, and preferably 0.50~ 0.60%.
Mo：Molybdenum is the core intensified element in carbide and steel of the present invention, and molybdenum can improve in steel The quenching degree of steel, while special carbide is formed in steel, improve the post-curing ability and temper resistance of steel.This hair In bright steel, in order to control the quantity of VC primary carbides, content of vanadium reduces, and in order to not influence the post-curing ability of steel, improves The content (1.80~2.80%) of molybdenum element, and preferably 2.10~2.60%.It is demonstrated experimentally that increased molybdenum more with carbon knot It closes, more tiny rod-short Mo is precipitated in tempering2C carbide has played raising steel belt roof bolt stability of the present invention very big Effect.
Mn：Manganese has the function of solution strengthening in steel, so as to improve the intensity of mould steel and hardness, and improves steel Quenching degree can also eliminate the adverse effect of sulphur, and control Mn contents are in 0.6-0.9% in the present invention.
Si：Silicon is present in ferrite or austenite with being dissolved volume morphing as the alloying element in steel, does not form carbon Compound improves annealing, normalizing and hardening heat, improves quenching degree.Since silicon has facilitation, and steel of the present invention to segregation Middle molybdenum content reaches 1.80~2.80%, and diffusion coefficient of the molybdenum element in steel is larger, and microstructure homogenization is difficult, easily makes in steel Banded structure is formed, the tropisms such as causes low, therefore, suitably reduces silicone content on the basis of H13 steel, silicon in steel of the present invention Content control 0.30~0.60%.
Ni：Nickel is austenite stabilizer element, is played an important roll for the quenching degree for improving steel, steel of the present invention is set The content of chromium is reduced in meter thinking, affects the quenching degree of steel to a certain extent, in order to make mold made of the steel real Existing section enlargement, design are added to nickel element.Nickel element content range 0.80~1.40%, preferably 0.80 in steel of the present invention ~1.20%, based on following result of study：
(1) nickeliferous 1%, the critical point of steel reduces by 40~50 DEG C or so relative to not nickeliferous H13 steel.CCT curve is right It moves, the critical cooling rate of martensite transfor mation is caused to be reduced to 500 DEG C/h by 4170 DEG C/h, greatly improving quenching degree (is The big section of mold and the important evidence for making center portion holding high intensity), but continue to increase nickel content, it does not produce bigger effect.
(2) nickel of addition 1% or so can improve high tempering hardness and elevated temperature strength in steel, but continue to increase nickel content, Hardness and elevated temperature strength increase unobvious.
Al：Aluminium is ferrite former, and non-carbide formation element is not involved in forming carbide, but can promote Ovshinsky Body promotes carbide to be formed, so can promote post-curing effect to martensite transfor mation.Aluminium improves A3 temperature, reduces γ and stablizes Phase region.Aluminium possesses the effect that nitrogen is determined in deoxidation in steel-making, and adding in a small amount of aluminium base originally will not occur the intensity of alloy, hardness Variation, but oxidation-resistance property enhances；The aluminium of addition proper content can form the Ni in Dispersed precipitate in the base3Al gold Compound between category can improve yield strength and elevated temperature strength.In practical application, aluminium content easily causes liquation carbon higher than 0.6% The segregation of the non-metallic inclusion of compound reduces impact flexibility.Ni constituent contents in steel of the present invention control adding for aluminium Enter amount 0.3~0.6%, and further preferred 0.3~0.5%.
Co：Cobalt is mainly dissolved in the base, and carbide is hardly formed in steel, and only minimal amount of cobalt atom can be into Enter into precipitated phase, therefore, cobalt mainly plays solution strengthening, improves high temperature corrosion resistance and antioxidation under high temperature.Cobalt is being tempered Or the aggregation of other element alloy carbides is prevented, delayed during use.In steel of the present invention, the addition of cobalt is to delaying chromium carbon Compound aggregation roughening has certain effect, it is thus possible to improve the temper resistance of hot die steel.Cobalt is that steel of the present invention is special Important element, content control determine to grind based on following in 0.50~1.10%, preferably 0.50~0.80%, composition range Study carefully achievement：
(1) traditional theory is thought, the addition of cobalt reduces impact flexibility, and steel of the present invention is found in the process of development：0.45% Under the alloy system of+3% chromium of carbon, cobalt content changes in the range of 0~3%, the trend that impact flexibility is improved.
(2) cobalt content reaches 0.50%, the anti-oxidant weightless ability enhancing of steel.
Under the alloy system of+3% chromium of (3) 0.45% carbon, cobalt content is more than 0.50~1.10%, and tempering hardness, tension are strong Degree, elevated temperature strength no longer change substantially.Therefore, steel of the present invention is under the alloy system of 3% chromium, cobalt content ratio range 0.50 ~1.10%, preferably 0.50~0.80% to reach best combination of strength and toughness.
Rare earth element:The rare earth element added in steel of the present invention is mainly Ce or La elements, on the one hand generates deoxidation, goes On the other hand the effect of sulphur, cleaning molten steel changes the Al formed due to the addition of aluminium2O3Inclusion morphology improves tissue, inhibits Carbide is in crystal boundary forming core, improvement impact flexibility.Steel Rare-Earth Content is too high, no longer generates apparent beneficial effect, and make into This increase.Steel rare earth elements control range 0.002~0.008%, preferably 0.002~0.006% of the present invention.
S：Sulphur is easily combined in steel with manganese, forms non-metallic inclusion MnS, along processing side usually in hot procedure To being elongated to as strip, large effect is generated to the transverse toughness of steel, reduces the equal orientation performance of steel, element sulphur is in warm Make to be often referred to as harmful element in mould steel, therefore, should be reduced as possible in the case where metallurgy condition allows, the present invention Sulfur content should be controlled 0.006% hereinafter, it is preferred that less than 0.003% in steel.
P：Phosphorus forms microsegregation in solidification of molten steel, and then when austenitizing temperature heats, segregation in crystal boundary, makes steel Brittleness significantly increase.Control phosphorus content 0.01% hereinafter, and content it is more lower better.
The invention has the advantages that with higher heat resistance, impact flexibility and quenching degree, it is particularly suitable for making requirement height Big section, that is, section thickness of heat resistance and impact flexibility is more than 400mm hot forged moulds.
Description of the drawings
Fig. 1 is the spheroidizing organization chart of steel of the present invention.
Fig. 2 is steel of the present invention and the temper resistance comparison diagram of compared steel.
Specific embodiment
According to above-mentioned designed chemical composition ranges, using 3 stove of vacuum induction furnace smelting steel of the present invention and 1 stove pair Than steel (H13), specific chemical composition is as shown in table 1.Molten steel casting ingot, and after 1240 DEG C keep the temperature 10h High temperature diffusions, 1150 DEG C of heating and thermal insulation 2h are cooled to, 1100~1150 DEG C are opened forging, final forging temperature >=900 DEG C, and total forging ratio >=6 are madeBar.Steel forging base of the present invention is warming up to 900~1000 DEG C with stove, the homogenization organized after being forged, It after keeping the temperature 4h, is air-cooled to 450 DEG C of hot chargings and enters stove, after 860 DEG C of heat preservation 4h, be cooled to 730 DEG C of heat preservation 8h and be furnace-cooled to 500 DEG C It comes out of the stove below air-cooled.After annealing, sample is processed into, through quenching, temper (1030 DEG C quenching, 510~650 DEG C tempering), room Warm mechanical property is shown in Table 2~4, and mechanical behavior under high temperature is shown in Table 5, and the temper resistance of steel of the present invention and compared steel is shown in Fig. 2.
Steel of the present invention has the characteristics that compared with compared steel：
1st, through 1030 DEG C quenching, 510~650 DEG C tempering after, steel hardness of the present invention higher than compared steel, especially 600~ After 650 high temperings, tempering hardness is higher by 5HRC or so than compared steel, has higher tempering resistance (being shown in Table 2)
2nd, through 1030 DEG C of quenchings, after each high-temperature tempering, steel tensile strength of the present invention is higher than compared steel (being shown in Table 3).
3rd, after 1030 DEG C of quenchings, when less than 570 DEG C of tempering, impact flexibility (is shown in Table steel of the present invention higher than compared steel 4)。
4th, elevated temperature strength (including tensile strength and yield strength) of the steel of the present invention at a temperature of same test is higher than comparison Steel has higher heat resistance (being shown in Table 5)
5th, hot die steel of the present invention carries out temper resistance under the conditions of 600 DEG C and 650 DEG C with compared steel (H13 steel) Contrast experiment, by the quenching of two steel, tempering hardness is adjusted to 45HRC or so, and result of the test is as shown in Figure 2.By attached drawing 2 it is found that When being tempered for a long time for 600 DEG C, steel belt roof bolt hardness of the present invention is slightly above compared steel, but at 650 DEG C, with tempering time Extension, compared steel hardness drastically declines, and is tempered 24 hours, and steel belt roof bolt hardness of the present invention is higher by a compared steel 5HRC left sides The right side has higher temper resistance.
The chemical composition of 1 steel embodiment of the present invention of table and compared steel, weight %
Steel grade C Si Mn Cr Mo V P S Co Ni Al Ce Fe
Steel 1# of the present invention 0.45 0.35 0.66 3.47 2.43 0.55 0.006 0.004 0.55 0.91 0.38 0.0030 It is remaining
Steel 2# of the present invention 0.44 0.32 0.65 3.60 2.41 0.60 0.006 0.003 0.73 0.97 0.40 0.0040 It is remaining
Steel 3# of the present invention 0.47 0.38 0.64 3.51 2.71 0.55 0.006 0.004 0.63 0.92 0.41 0.0036 It is remaining
Compared steel 0.38 1.03 0.45 4.88 1.31 1.01 0.008 0.003 / / It is remaining
The hardness number of 1030 DEG C of quenching different temperatures tempering of 2 steel embodiment of the present invention of table and compared steel
The tensile strength table of 3 steel embodiment of the present invention of table and compared steel
The U-shaped notch impact toughness table of 4 steel embodiment of the present invention of table and compared steel
The elevated temperature strength performance data table of 5 steel embodiment of the present invention of table and compared steel

Claims (4)

1. a kind of hot forging high heat-intensity, high impact toughness hot die steel, which is characterized in that chemical component weight % is as follows For：C:0.40~0.50%, Si:0.30~0.60%, S≤0.006%, P≤0.01%, Mn:0.60~0.9%, Mo:1.80 ~2.80%, Cr:3.00~3.80%, V:0.40~0.60%, Ni:0.80~1.40, Al:0.3~0.6%, Co:0.50~ 1.10%, rare earth element (Ce+La):0.002~0.008%, surplus is Fe and inevitable impurity.
2. hot die steel as described in claim 1, which is characterized in that the specific chemical composition weight % of the steel is：S≤ 0.003%, Mo:2.10~2.60%, Cr:3.20~3.50%, V:0.50~0.60%, Ni:0.80~1.20, Co:0.50 ~0.80%, rare earth element (Ce+La):0.002~0.006%.
3. a kind of preparation method of the hot die steel described in claims 1 or 2, it is characterised in that including following High temperature diffusion and Forging technology：
Heating Steel Ingots homogenize ingot composition to 1200 DEG C~1250 DEG C 10~15h of High temperature diffusion；It is directly cooled to after diffusion 1140 DEG C~1180 DEG C 2~4h of heat preservation, 1050~1100 DEG C are opened forging, are processed using multiway forging, total forging ratio 6~7, finish-forging 900~950 DEG C of temperature, slow cooling to room temperature.
4. preparation method as claimed in claim 3, which is characterized in that including following normalizing and annealing process：
Forging stock is warming up to 900 DEG C~1000 DEG C with stove, the homogenization organized after being forged, after keeping the temperature 4h, be air-cooled to 400 DEG C~ 500 DEG C of hot chargings enter stove, after 840 DEG C~860 DEG C 4~6h of heat preservation, are cooled to 710~740 DEG C of 8~12h of heat preservation and are furnace-cooled to 500 It comes out of the stove below DEG C air-cooled.
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CN113122782A (en) * 2021-04-21 2021-07-16 浙江中煤机械科技有限公司 Stainless steel for pump head body and preparation method thereof
CN113174540A (en) * 2021-04-28 2021-07-27 重庆大学 Low-cost die forged steel base material, sandwich layer forging die and preparation method thereof
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CN114941061A (en) * 2022-05-16 2022-08-26 洛阳中重铸锻有限责任公司 Heat treatment method for steel forging of hot-working die with ultra-thick section
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CN116334496A (en) * 2023-04-28 2023-06-27 鞍钢股份有限公司 Die steel with fine eutectic carbide and preparation method thereof
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