CN106435353A - Cr5 series hot work die steel - Google Patents
Cr5 series hot work die steel Download PDFInfo
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- CN106435353A CN106435353A CN201610717357.0A CN201610717357A CN106435353A CN 106435353 A CN106435353 A CN 106435353A CN 201610717357 A CN201610717357 A CN 201610717357A CN 106435353 A CN106435353 A CN 106435353A
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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
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
- C21D1/32—Soft annealing, e.g. spheroidising
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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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
- C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
- C22C38/105—Ferrous alloys, e.g. steel alloys containing cobalt containing Co and Ni
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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
- 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
- C21D2211/004—Dispersions; Precipitations
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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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Abstract
The invention provides Cr5 series hot work die steel which comprises, by weight, 0.40-0.48% of C, 0.20-1.2% of Si, 0.40-0.80% of Mn, no more than 0.020% of P, no more than 0.010% of S, 4.80-5.50% of Cr, 1.40-2.0% of Ni, 0.80-1.50% of Mo, 0.50-0.70% of V, 0.50-1.00% of W, 0-0.75% of Co, 0.01-0.20% of Al, 0.02-0.20% of Nb, and the balance Fe. The chemical composition formula of the novel Cr5 series hot work die steel provided by the invention is recorded as the YB5 series, and compared with existing Cr5 series (H13) hot work die steel, the YB5 series die steel is higher in C content and Mn content and lower in Si content (YB5A and YB5C), Mo content and V content, and Ni, W, Co (YB5C) and Al (YB5A and YB5C) are added. Accordingly, the toughness of the steel is improved, and the high-temperature strength and creep resistance are improved.
Description
Technical field
The invention belongs to ferrous alloy field, and in particular to a kind of alloy and its preparation and application for forging mold.
Background technology
Mould is the main technique equipment of die forging, and its life-span directly affects quality, cost and the efficiency of forging.Forging die expense
Account for 30%～45% (note of forging cost:Because forging batch is little, therefore forging die cost accounting is big).Due to forging high-temperature alloy mold
Service condition is poor, and mold cavity bears very big impulsive force, and the long period is in more than 550 DEG C of hot environment, and mould becomes
Shape, wear and tear, collapse angle and problem of subsiding be than more serious.
5CrNiMo and 5CrNiMoV are major die material in current industrial (GB/T11880-89 die hammers and large-scale
Mechanical forging press building block technique condition)；GB1299-2000 alloy tool steel；《China's hot die steel performance data collection》, Zhu
Zong Yuan, mechanical engineering material, the 12nd phase of volume 25, P12).Wherein 5CrNiMo mould steel heat resistance and wearability are poor, mould
More than 500 DEG C of hot environment should not be chronically at, for example on 4000t forging equipment, 5CrNiMo mould steel is using having no different
Often, die wear but on 1.8 ten thousand tons and 3.55 ten thousand tons big hammering equipment, collapse angle and problem of subsiding then more serious.
5CrNiMoV is the large-scale hammering mold materials of beginning popularization and application in 2013,5CrNiMoV mould steel heat resistance and wearability phase
To preferable, the needs of blade process of steel forging dies can be met substantially, but mould should not be chronically at more than 550 DEG C of hot environment.
JBD275 is the technique diskware of GH4169 alloy direct aging acquisition, can produce in enormous quantities, the technique diskware mould
During forging, the deformation of mould center portion is serious, has had a strong impact on forging overall dimensions and product inherent quality, the high efficiency production to product
Larger challenge is all brought with batch stability.Solve the problems, such as that die deformation has become as the task of top priority of diskware forging.
China's forging is of less types with mold materials, apply most be 5CrNiMo in GB/T11880-89,
5CrNiMoV、4Cr2MoVNi(B2)；H13 in GB/T1299-2000；According to being weighed using hardness in these kinds, high
Height, low is low, lacks the kind of middle hardness, and the 5Cr2NiMoVSi in GB/T11880-89 belongs to the moderate kind of hardness, but
Because fragility is big, it is easy to ftracture, apply not extensive.Therefore need to develop alloying and hardness in the middle of 5CrNiMo and H13 or be higher than
The series of products of H13.5CrNiMo is GB Die Steel Products, it is adaptable to using hardness HRC42-47 (small-sized), HRC39-44
(middle-size and small-size), the steel of HRC37-42 (medium-sized), (《Mold materials application manual》, Lin Huiguo, fire tree roc, Ma Shao are more edited, mechanical
Industrial publishing house's second edition, P14, P32), purposes simple shape, thickness 250-350mm.The steel alloying is relatively reasonable, in forging
When making resistance of deformation little low-alloy steel, application effect is preferable.If for more heavy in section or higher temperature hot-forging die when, this
Kind steel is low due to quenching degree and hardenability, and heat stability is poor, and causes the mold use life-span low.
H13 (4Cr5MoSiV1) is the most widely used high-alloy hot work mould steel in the world, and purposes has die cavity complexity, bears
The larger hammer forging die of shock loading, the unitary mould on forging press or insert, and hot extrusion mould, hot-cutting die, compression mod
Deng, with higher thermohardening and wearability (《The application of H13 mould steel and development》, Li Caiwen, Wang Mengjun, military star, China
Material science and technology and equipment, 2009, the 4th phase).One steel grade in the H13 Gang Yuanshi U.S., is commonly referred to as 4Cr5MoSiV1 in China
Steel.Hot die steel requires that material has high quenching degree, high elevated temperature strength, high wearability, high toughness, high heat resistanceheat resistant
Split ability and high resistance to melting loss performance etc..Why H13 steel is widely used, and is because that it has following characteristic：1. there is height
Quenching degree and high toughness；2. excellent thermal crack resistant ability, can give water-cooled in workplace；3. have medium wear-resisting
Property, carburizing or nitridation process can be adopted to improve its case hardness；4. there is anti-softening ability at relatively high temperatures；5. heat treatment
Deformation is little；6. good machinability.The shortcoming of H13 is to be not suitable for manufacturing big-and-middle-sized, large-scale and ultra-large type mould, easily
In cracking.Heavy in section hot die steel is developed in native land.
Thickness >=350～the 500mm of forging and stamping module is referred to as heavy die block, the super-huge module of the title of thickness >=500mm.I
State develops 45Cr2NiMoVSi (45Cr2), 5Cr2NiMoVSi (5Cr2), 3Cr2MoVNi (B2) and 3Cr2MoWVNi (B3)
(JBT8431-1996 《Hot forging forming mould steel and its heat treatment technics condition》) etc. heavy in section hot die steel, with 5CrNiMo
Compare, 45Cr2 and 5Cr2 steel improves quenching degree, elevated temperature strength, heat stability, and impact flexibility is suitable, heat wear resistance and anti-
The performance of heat exhaustion is also better than 5CrNiMo, (《Mold materials application manual》, Lin Huiguo, fire tree roc, Ma Shao more edit, mechanic
The industry publishing house second edition, P410).But 45Cr2 and 5Cr2 are easy to cracking.
Content of the invention
For the problem that this area is present, it is an object of the present invention to provide one kind is suitable to heavy die block and super-huge module Cr5
Serial hot die steel.
Second object of the present invention is the preparation method for proposing the Cr5 series hot die steel.
Third object of the present invention is the method for proposing to prepare mould with Cr5 series hot die steel.
The concrete technical scheme for realizing above-mentioned purpose of the present invention is：
A kind of Cr5 series hot die steel, it is characterised in that the hot die steel in terms of weight %, comprising C0.40～
0.48%, Si 0.20～1.2%, Mn 0.40～0.80%, P≤0.020%, S≤0.010%, Cr4.80～5.50%, Ni
1.40～2.0%, Mo0.80～1.50%, V0.50～0.70%, W0.50-1.00%, Co 0～0.75%, Al0.01～
0.20%, Nb 0.02～0.20%, the Fe of surplus；
The preparation method of the novel C r5 series hot die steel, including step：
Electric furnace or converter smelting, LF stove refine (LADLE FURNACE is ladle refining furnace), vacuum outgass (VD), molding,
Anneal, electroslag remelting (ESR), slow cooling, annealing, forge, normalizing, spheroidizing, expansion hydrogen, slightly add, inspection, slightly add, quenched, smart
Plus, inspection.Operation obtains module or mould.
In prior art, the main alloy element of hot die steel and scope are:C0.26-0.75%, Si0.10-
1.2%th, Mn0.20-1.60%, Cr0.5-5.5%, Mo0-3.4%, W0-7.9%, V0-1.4%, Ni0-4.3%, Co0-
4.5%th, AL0-0.7%, Nb0-0.3%, the change of each component content the tissue of steel and performance are played beneficial effect and
Unfavorable effect, the present invention takes the normal place of each element, evades its weakness, and the aspect of emphasis consideration is as follows：
1) effect of the C in steel
Expansion γ phase region, but the formation because of cementite, it is impossible to unlimited solid solution；With the increase of content, improve steel hardness and
Intensity, but reduce its plasticity and toughness.Improve the quenching degree of steel；
For improving the wearability of steel, steel should be made to obtain martensite+alloy carbide tissue, the steel containing chromium 5%, 870 DEG C of Austria
During family name's body, in austenite A and A+M3C+M7C3 intersection, phosphorus content is 0.4-0.5%, therefore selects the phosphorus content of 0.4-0.5%,
It is maintained in the level to form a certain amount of alloy carbide,
Reduce Ms point, therefore relatively low carbon content is kept, make the Ms of steel that of a relatively high level is taken at, Ms340 DEG C, quench
Martensite+residual A+C, and tempered rear acquisition uniform martensitic structure is obtained when fiery, obtains lath martensite+a small amount of lamellar M+
A small amount of remnants A.
Therefore steel grade of the present invention takes C0.40～0.48%.
2) effect of the silicon in steel:
(1) improving the intensity of solid solution and cold work hardening degree in steel reduces the toughness of steel and plasticity.
(2) Si is that the effective element .Si for improving resistance to tempering reduces diffusion velocity of the carbon in ferrite, separates out tempering
Carbide be difficult aggregation, increased temper resistance；
(3) high-temperature oxidation resistance of steel is improved；
(4) unfavorable aspect easily makes steel assume banded structure, reduces the lateral performance of steel.
The development trend of Cr5 Series Die Steel is developed to the high Mo direction of low Si at present.The detrimental effect of Si is mainly and increases
Biasing is analysed, and increases eutectic carbide.Therefore Si takes 0.20～0.40% satisfaction smelting deoxidation demand water in YB5A, YB5C of the present invention
Flat, wherein YB5B takes 0.40～1.0% for high Si, mainly uses which and improves intensity, antioxidation, improves temper brittleness temperature
Effect, its unfavorable effect can be controlled by by taking smelting and heating technological measure.YB5B can be used to manufacture low impact
The mould of power.
Therefore steel grade of the present invention takes Si0.20～0.40% and 0.40～1.0% two kind of level.
3) effect of the manganese in steel
(1) manganese improves the quenching degree of steel.
(2) manganese and ferrum form solid solution, improve the hardness and intensity of ferrite and austenite in steel, and Mn can form carbonization again
Thing, so as to improve intensity, hardness and the wearability of steel.
(3) manganese is increased to the high-temperature instantaneous intensity of steel.
(4) manganese reduces the Ms point of steel strongly, increases the remained austenite content in hardened steel, and favourable aspect can improve tough
Property, can disadvantageously increase deflection；
The major defect of manganese steel is, 1. containing manganese higher when, have obvious temper brittleness phenomenon；2. manganese has promotion crystal grain long
Big effect, therefore manganese steel is to overheated more sensitive, therefore must be noted that in Technology for Heating Processing.This shortcoming can refine crystalline substance with adding
Grain element such as molybdenum, vanadium, titanium etc. is overcoming.
Mn is good deoxidizer and desulfurizing agent, and Mn must reach a certain amount in steel, and Mn/S is have to be larger than equal to 8.
Therefore invention steel grade Mn takes 0.40～0.80%.
4) effect of the chromium in steel
(1) chromium can improve intensity and the hardness of steel.(2) chromium can improve the high-temperature mechanical property of steel.(3) have steel good
Corrosion resistance and non-oxidizability.(4) prevent graphitization.(5) quenching degree is improved.(6) carbide is formed, improves wearability.(7)
Increase temper resistance.
During the chromium of addition ＜ 6%, the tempering resistance of steel is improved a lot, but post-curing is not reached into, as chromium ＞
When 6%, steel occurs post-curing effect in 550 DEG C of tempering after quenching, and old friends are general to hot die steel to select 5% chromium
Addition.
Impact and Mn of the Cr to steel eutectoid point is substantially similar, and in about 5% chrome content, the C content of eutectoid point is dropped to
0.5% or so.In addition the addition of Si W Mo V more significantly reduces eutectoid point C content.For this it is known that：4Cr5 series of heat is made
Mould steel belongs to hypereutectoid steel.The reduction of eutectoid C content, will increase the alloy carbon after austenitizing in the last tissue of tissue neutralization
Compound content.
Shortcoming：1. chromium is to significantly improve the brittle transition temperature of steel 2. chromium can promote steel belt roof bolt fragility.
Therefore steel grade Cr of the present invention takes 4.80～5.50%.
5) effect of the nickel in steel
(1) intensity of steel can be improved, and its toughness is improved, improve fatigue resistance.(2) nickel can reduce the Transition of Brittleness temperature of steel
Degree, you can improve the low-temperature flexibility of steel.(3) nickel can improve the resistance to corrosion of steel, can not only be acidproof, and can alkali resistant and big
The corrosion of gas.(4) quenching degree is improved, and (5) expand austenitic area, increase the remained austenite content in hardened steel, favourable aspect
Toughness can be improved, can disadvantageously increase deflection；(6) increase dendrite, improve lateral performance；(7) increase lath-shaped horse
Family name's scale of construction, improves toughness；(8) accelerating diffusion of the carbon in austenite, Ni forms element for non-carbide, carbon is improved in austenite
In diffusion coefficient, reduce primary carbide, and make proeutectoid carbide be difficult to grow up.(9) Ni makes the layer of austenite arrange to carry
High.It is generally acknowledged that layer arrange can be lower, the extension that is more conducive to position to arrange and form position and arrange, make sliding difficulty, cause the processing of steel hard
Change trend increases.Otherwise layer is arranged can be higher, more easily deformable processing.This can increase forging pass deformation, be conducive to tissue to break
Broken and loose seam.
Therefore steel grade Ni of the present invention takes 1.40～2.0%.
6) effect of the molybdenum in steel
(1) molybdenum has solution strengthening effect to ferrite.(2) steel heat resistance is improved, improves elevated temperature strength.Keep in high temperature
Enough intensity and creep resisting ability (be stressed at high temperature for a long time, deform, claim creep).(3) crystal grain thinning, improves
Toughness.(4) quenching degree of steel is improved.(5) post-curing effect is played, and addition is not less than 1%, highest 3%.(6) carbon is formed
Compound, improves wearability.(7) increase temper resistance.(8) steel belt roof bolt fragility can be suppressed.
Shortcoming：The main ill effect of molybdenum is that it can make low-alloy molybdenum steel that graphited tendency occurs.
Therefore steel grade Mo of the present invention takes 0.80～1.50%.
7) effect of the vanadium in steel
(1) steel heat resistance is improved.(2) crystal grain thinning.(3) post-curing effect is played, and (4) form carbide, improve resistance to
Mill property.Shortcoming：V is high to form primary carbide, and solution temperature is high, not readily dissolves, so as to reduce toughness.
Therefore steel grade V of the present invention takes 0.50～0.70%.
8) effect of the tungsten in steel
(1) increase temper resistance；(2) increase red hardness；(3) increase heat resistance, the adhesion of atom is improved, improve and expand
Scattered activation energy and activation energy of creep, improve stability and the creep resistance of tissue.(4) carbide is formed, improves wearability；(5)
Post-curing effect is played, (6) improve quenching degree, can suppress steel belt roof bolt fragility.
Therefore steel grade W of the present invention takes 0.50～1.00%.
9) effect of the aluminum in steel
(1) reinforced ferrite；(2) high temperature hardness is improved；(3) solid solution strength is improved；(4) crystal grain thinning；(5) Ms is improved
Point, increases lath M.(6) element being formed for non-carbide, can improve the activity of carbon, improves Carbon diffusion coefficient, make secondary carbonization
Thing is difficult to grow up.
Therefore steel grade Al of the present invention takes 0.01～0.04% and 0.06～0.20% two kind of level.
10) effect of the cobalt in steel
Cobalt forms element for non-carbide in steel, is dissolved in austenite, is present in martensite after quenching during Quench heating
In, the anti-temper resistance of martensite is improve, secondary hardening effect is strengthened, have preferable thermohardening.Cobalt and tungsten, molybdenum original
The adhesion of son is strong, can lower the diffusion velocity of tungsten, molybdenum atom, slows down alloy carbide and separates out and agglomeration, increased heat
Rigid.Which disadvantageously has reduction toughness, reduces quenching degree.
Therefore steel grade Co of the present invention takes 0.00～0.20% and 0.50～0.75% two kind of level.
11) effect of the niobium in steel
Nb and C, N, O have extremely strong affinity, form extremely stable compound therewith, improve the hardness of steel.While more
Scattered compound with crystal grain thinning, can improve the Coarsening Temperature of crystal grain, reduce superheated susceptivity and the temper brittleness of steel.
Therefore steel grade Nb of the present invention takes 0.020～0.2% level.
12) other elements and gas content：Cu：Carbide is not formed, is present in matrix with solid solution state, steel can be improved
Toughness, improves quenching degree and corrosion resistance.But its shortcoming is to increase the red brittleness of steel, therefore its content controls in≤0.20% water
Flat.Ti：For carbide former, can crystal grain thinning, similar with the effect of V, Nb, due to the addition of V and Nb, therefore Ti does not add
Plus, should control in≤0.01% level.P, S, Pb, Sn, As, Sb, Bi and gas content N, H, O are harmful element, all should control
System is in reduced levels and more low better.
Specifically, the hot die steel is in terms of weight %, comprising C0.40～0.48%, Si 0.20～0.40%, Mn
0.40～0.80%, P≤0.020%, S≤0.010%, Cr4.80～5.50%, Ni1.40～2.0%, Mo0.80～
1.50%, V0.50～0.70%, W0.50-1.00%, Al0.06～0.20%, Nb0.02～0.20%, the Fe of surplus.This
Steel is designated as YB5A, and in composition, Si is low, toughness height.
Or, the hot die steel is in terms of weight %, comprising C0.40～0.48%, Si 0.40～1.0%, Mn 0.40
～0.80%, P≤0.020%, S≤0.010%, Cr4.80～5.50%, Ni1.40～2.0%, Mo0.80～1.50%,
V0.50～0.70%, W0.50-1.00%, Al0.01～0.04%, Nb0.02～0.20%, the ferrum of surplus.This steel is designated as
YB5B, in composition, Si is higher, and hardness is slightly higher.
Or, the hot die steel is in terms of weight %, comprising C0.40～0.48%, Si 0.20～0.40%, Mn 0.40
～0.80%, P≤0.020%, S≤0.010%, Cr4.80～5.50%, Ni1.40～2.0%, Mo0.80～1.50%,
V0.50～0.70%, W0.50-1.00%, Co 0.50～0.75%, Al0.06～0.20%, Nb0.02～0.20%, surplus
Ferrum.This steel is designated as YB5C, contains Co, anti-temper resistance high and thermostability height in composition.
A kind of preparation method of alloy mold, the alloy mold is high temperature alloy mould, blade steel mold and low-alloy
One kind in steel mold, with hot-work die steel making of the present invention, including step：
S1 quenches：≤ 650 DEG C of shove charges, isothermal at a temperature of being maintained at 650 DEG C, 800～820 DEG C of isothermals are warming up to stove, etc.
The warm time presses effective dimensions 0.6min/mm of workpiece and calculates, then is warming up to 1000～1020 DEG C with stove, is kept for 10～12 hours,
Oil cooling be cooled to 150～180 DEG C fuel-displaced after be tempered immediately；
S2 is once tempered：≤ 280 DEG C of shove charges, 4～10h of isothermal at a temperature of being maintained at 280 DEG C, 570～595 DEG C are warming up to,
Keep 14～22h (such as 570～580 DEG C of diskware/holding 15h；585～595 DEG C of blade/holding 21h.Less than 550 DEG C hardness
What high, fragility was big can not be with the temperature below this), oil cooling is cooled to air cooling after 100～150 DEG C of surface temperature (can not water-cooled), goes out
During oily air cooling, it is ensured that mould can just carry out second tempering after being cooled to room temperature；
S3 double tempering：≤ 300 DEG C enter stove, 560 DEG C of holding 12h of diskware, or 580 DEG C of holding 18h of blade, are air cooled to 100
Below DEG C.
The effective dimensions of workpiece for round piece, can refer to its diameter, for square cross, refer to which also known as equivalent size
Thickness, cake part, workpiece with holes etc., depending on can looking into heat treatment handbook.It is related to what the time was measured with "/mm " in the present invention, is all
Refer to based on the effective dimensions of workpiece.
Specifically, the alloy mold is high temperature alloy mould or blade steel mold, and its preparation method also includes：
Tri- tempering of S4：≤ 300 DEG C enter stove, and 580 DEG C of temperature keep 1.8min/mm (closing this step of knot to omit).Diskware
560 DEG C of holding 10h, 580 DEG C of holding 16h of blade, air cooling is cooled to room temperature carries out Rockwell hardness detection.
Wherein, in step sl, isothermal 0.6min/mm at a temperature of being maintained at 650 DEG C, is warming up to 800～820 DEG C of guarantors with stove
0.6min/mm is held, then 1000～1020 DEG C of 1.0～1.2min/mm of holdings (such as diskware 12h, blade 10h) is warming up to stove；
High temperature alloy mould (diskware) 80～90min of oil cooling, or blade 120～130min of oil cooling, be cooled to 150～180 DEG C fuel-displaced after
It is tempered immediately；
In step s 2, diskware keeps diskware 15h in 570～580 DEG C of temperature, or blade is kept in 585-595 DEG C of temperature
21h, oil cooling is cooled to air cooling after 100～150 DEG C of surface temperature, during fuel-displaced air cooling, it is ensured that mould can just carry out after being cooled to room temperature
The double tempering of S3；
In step s3,560 DEG C of temperature of diskware keep diskware 12h, or blade keeps 18h at 580 DEG C, is air cooled to 100 DEG C
Third time tempering is below carried out；
In step s 4,560 DEG C of temperature of diskware keep 10h, or 580 DEG C of holding 16h of blade.
Preferably, in step sl, isothermal 0.6min/mm at a temperature of being maintained at 650 DEG C, is warming up to 820 DEG C of holdings with stove
0.6min/mm, then 1000～1020 DEG C of 1.0～1.2min of holding are warming up to stove, oil cooling (determines according to the size of block, for example
Oil cooling 120～130min of blade), be cooled to 150～180 DEG C fuel-displaced after be tempered immediately；
In step s 2,2.4～3.0min/mm are kept in 585～595 DEG C of temperature, oil cooling be cooled to surface temperature 100～
Air cooling after 150 DEG C, during fuel-displaced air cooling, it is ensured that mould carries out the double tempering of S3 after being cooled to room temperature；
In step s3,580 DEG C of temperature keep 1.8～2.4min/mm, and being air cooled to less than 100 DEG C carries out third time tempering.
Quenched is that quenching Jia two to three high temperings.It is situated between with the heating-up temperature required by S1～S4, heat time heating time, cooling
Matter, cool time, final cooling temperature carry out primary quenching process, two to three temper.
Wherein, after step S3 double tempering or after tri- tempering of S4, air cooling is cooled to room temperature carries out Rockwell hardness detection, for
The hardness requirement of high temperature alloy (diskware) mould is：Case hardness is maximum no more than 52HRC, and minimum cannot be below 42HRC；Right
The hardness requirement of steel mold is tied in blade steel mold and conjunction：Case hardness is maximum no more than 48HRC, and minimum cannot be below
38HRC.
Mould obtained in preparation method of the present invention.
The beneficial effects of the present invention is：
1), a kind of chemical composition of new Cr5 series hot die steel (being designated as YB5 Series Die Steel) of present invention proposition is joined
Side, is compared with existing Cr5 system (H13) hot die steel, and YB5 Series Die Steel improves carbon content, improves Mn content, drop
Low silicone content (YB5A, YB5C), reduces Mo content, reduces V content, with the addition of Ni element, with the addition of W element, interpolation
Co element (YB5C), with the addition of Al element (YB5A, YB5C).So as to the toughness of steel is improve, improve elevated temperature strength and resist
Croop property etc..
2), present invention proposition YB5 Series Die Steel is reasonably smelted, heats, forging and conditioning treatment technological specification.Close
Key point is the macrostructure densification for ensureing steel, and clarity is high, primary carbide and banding rank is low, normalizing (rapid cooling) is organized carefully afterwards
Change, after nodularization, carbide is tiny and uniform etc..
3), the present invention has worked out Final Heat Treatment Process specification.Its key point will fully for quenching cooling, and tempering is eliminated
Stress will be fully.Obtained YB5 hardness of steel and hardness are higher, show there is higher anti-temper resistance, 600 DEG C of tempering,
Hardness or mutual close with H13 height, its toughness is far above H13.
Description of the drawings
Fig. 1 is the hardness balance's figure under YB5A temperature different from H13.
Fig. 2 is high temperature alloy diskware mould test position schematic diagram.
Fig. 3 is three coordinate measurement figure of diskware mould.In Fig. 3, upper mould before (a) die forging, after (b) die forging before upper mould (c) die forging
Lower mould, lower mould after (d) die forging.
Fig. 4 is the three coordinate measurement figure of size comparison of lower mould before and after YB5A blade steel mold finish-forging.In Fig. 4, (a) blade is forged
Before making, after the forging of (b) blade, before the forging of (c) blade root, after the forging of (d) blade root.
Fig. 5, embodiment 4,150 × 300 sides, 1000 DEG C of 6h water, 760 DEG C of 9h water (quenched nodularization) are molten through 4% nitric acid ethanol
Corrosion, microscopic structure is tempered sorbite (amplifying 400 times).
Fig. 6 is YB5A φ 25mm sample, 1020 DEG C of oil, 580 DEG C of water, 580 DEG C of air-conditioning matter, and 4% nital corrodes
Afterwards, microscopic structure is secondary troostite (amplifying 400 times).
Fig. 7 is 560 × 260 sample of YB5A φ, 1010 DEG C of 570 DEG C of water, 570 DEG C of water skies (overall quenched), 4% nitric acid ethanol
After solution corrosion, microscopic structure organizes (amplifying 400 times) for secondary troostite.
Fig. 8 is YB5A230 × 300 sample, 1020 DEG C of oil, and after the corrosion of 4% nital, microscopic structure is thin lath
Martensite+carbide (amplifies 400 times).
Fig. 9 is 230 × 300 sample of YB5A, 1020 DEG C of oil, and after the corrosion of 4% nital, microscopic structure is thin plate
Bar martensite+10 grades of carbide grain degree (amplifies 400 times).
Figure 10 is YB5A φ 900mm × 300mm cake part, spheroidizing tissue after forging, after the corrosion of 4% nital,
Microscopic structure is sorbite+paralympic.A size of 100 μm of in figure institute target.
Figure 11 is 230 × 300 side of YB5A, and spheroidizing is organized, and 4% nital corrodes ferrite+spherical carburizing
Body AS6 level (amplifies 400 times).
Figure 12 is spherodized structure after the forging of 230 × 300 sample of YB5A, and 4% nital corrodes, and AS1 (amplifies 500
Times).
Spherodized structure after the forging of 230 × 300 sample of Figure 13 YB5A, 4% nital corrodes, and AS1 (amplifies 200
Times).
Note：Spherodized structure is by North America compression mod Metallographic standard NADCA#207-2003 collection of illustrative plates evaluation.
Specific embodiment
Following examples are used for the present invention to be described, but are not limited to the scope of the present invention.Described below is only the present invention
Preferred implementation, it is noted that for those skilled in the art, without departing from the technology of the present invention original
On the premise of reason, some improvements and modifications can also be made, these improvements and modifications also should be regarded as protection scope of the present invention.
In embodiment, if no special instructions, the technological means for being used are ordinary skill in the art means.
The composition range such as table 1 below of Cr5 Series Steel proposed by the present invention.A certain composition concrete is shown in an embodiment
Example, in the range of table 1 is recorded, obtained Cr5 series hot die steel has same performance.
Table 1：Become sectional specification：
Embodiment 1
The preparation method of Cr5 series hot die steel, it is characterised in that including step：Electric furnace smelting, LF stove refine
(LADLE FURNACE is ladle refining furnace), vacuum outgass (VD), molding, annealing, electroslag remelting (ESR), slow cooling, annealing, forging
Make, normalizing, spheroidizing, expand hydrogen, slightly add, inspection, finishing, quenched, finishing, inspection, go into operation.
By controlling the composition of molten steel, in obtained mould steel, in terms of weight %, comprising C0.44%, Si 0.40%, Mn
0.60%, P0.010%, S0.002%, Cr5.20%, Ni1.60%, Mo 0.90.%, V 0.60.%, W 0.55%, Co
0.09%, Al 0.10%, Nb 0.040%, the Fe of surplus.The product for obtaining is YB5A steel.
Embodiment 2
The method of smelting is with embodiment 1.By controlling the composition of molten steel, in obtained mould steel, in terms of weight %, comprising
C 0.43%, Si 1.00%, Mn 0.40%, P 0.012%, S0.0015%, Cr4.80%, Ni1.40.%, Mo1.00%,
V0.50%, W0.80%, Co 0.090.%, Al0.010%, Nb0.030%, the Fe of surplus.The product for obtaining is YB5B steel.
Embodiment 3
The method of smelting is with embodiment 1.By controlling the composition of molten steel, in obtained mould steel, in terms of weight %, comprising
C 0.43%, Si 0.40%, Mn 0.60%, P 0.009%, S0.001%, Cr 5.20%, Ni 1.60%, Mo1.10%,
V 0.60%, W 0.55.%, Co 0.53%, Al 0.20%, Nb 0.025%, the Fe of surplus.The product for obtaining is YB5C
Steel.
Embodiment 4
High temperature alloy mould is prepared with embodiment 1YB5A steel heat treatment, JBD275-YB5A- φ 900x300 is labeled as, system
For diskware mould.
S1 quenches：≤ 650 DEG C of shove charges, are warming up to 820 DEG C × (4 ± 0.5) h with stove by 650 DEG C × (2 ± 0.5) h isothermal, with
Stove be warming up to 1010 DEG C × (5 ± 0.5) h, 80～90min of oil cooling, fuel-displaced (in the air stop less than half an hour) immediately tempering；
The temperature of quenching is 1000 DEG C, the temperature (see the table below) of air cooling when comparing tempering, it is seen that 550 DEG C of tempering, YB5A
Intensity and hardness are higher, show there is higher anti-temper resistance, 600 DEG C of tempering, and hardness is more lower slightly than H13, and its toughness is far high
In H13 (note：As the hardening heat of YB5A is lower slightly less than H13 event hardness).
S2 is once tempered：≤ 280 DEG C of shove charges, 280 DEG C × (5 ± 0.5) h, be warming up to 570～580 DEG C × (15 ± 0.5h)
Oil cooling is cooled to air cooling after 100～150 DEG C of surface temperature, during fuel-displaced air cooling, it is ensured that mould can just carry out second after being cooled to room temperature
Tempering；
S3 double tempering：≤ 570 DEG C enter stove, and 570 DEG C × (13 ± 0.5) h is air cooled to less than 100 DEG C and can just carry out third time
Tempering；
Tri- tempering of S4：≤ 570 DEG C enter stove, 570 DEG C × (11 ± 0.5) h air cooling is cooled to room temperature carries out Rockwell hardness detection.
High temperature alloy die hardness is required：Case hardness is maximum no more than 52HRC, and minimum cannot be below 42HRC.
Tables 1 and 2 is shown in impact of the YB5A different heat treatment technique to mechanical property：
Table 1：
Table 2
It can be seen that optimal quenching temperature 1000-1020 DEG C, temperature is more than or equal to 550 DEG C.
(4) YB5A mechanical behavior under high temperature
Table 3
| Numbering | Matter technique processed | Test temperature | Rm/MPa | RP0.2/MPa | A, % |
| 71 | + 550 DEG C of κ 2h air coolings of 1000 DEG C of x1h oil coolings | 250℃ | 1725 | 1445 | 12 |
| 72 | + 550 DEG C of x2h air coolings of 1000 DEG C of x1h oil coolings | 300℃ | 1626 | 1390 | 12 |
| 73 | + 550 DEG C of x2h air coolings of 1000 DEG C of x1h oil coolings | 350℃ | 1627 | 1396 | 10.5 |
| 74 | + 550 DEG C of x2h air coolings of 1000 DEG C of x1h oil coolings | 400℃ | 1566 | 1346 | 10 |
It can be seen that its elevated temperature strength is higher, its hardness of conversion of tabling look-up more than or equal to HRC48 (during 350 DEG C of experimental temperature, still in
Higher level).The mechanical property of YB5A listed by table 4.
Table 4：Heat (batch) number 20506,40 side of specification, φ 25mm heat treatment test result
Analysis：1st, hardening heat rises high intensity and hardness rises；2nd, intensity and hardness of the water-cooled compared with air cooling is tempered for the first time
Rise.Therefore mould is tempered for the first time and answers rapid cooling.
Table 5:14506 specification of heat (batch) number, 40 side, the YB5A heat treatment test result of φ 25mm
Table 6:The YB5A heat treatment test result of 14510 specification of heat (batch) number, 40 side φ 25mm
Analysis：Contrast table 2 and table 3 are visible：Hardening heat is raised, and intensity and hardness rise, and percentage elongation slightly has reduction.Therefore quench
Fiery temperature should choose 1010～1020 DEG C.
Table 7:Heat (batch) number 14510, module, φ 25mm heat treatment test result
Note:189-1,189-2 are longitudinal performance；190-1,190-2 are lateral performance.
Analysis：From table 7：1020 DEG C of optimal quenching temperature.Microscopic structure is shown in Fig. 5～13, it is seen that spheroidizing is organized
Qualified, quenching structure is to improve strip of sheet martensite+choice refreshments shape carbide, with hardening heat, and silver broadens, and carbide is reduced,
Quenching hardness is raised, and after tempering, tempering hardness is also raised, and is organized as secondary troostite, 10 grades of grain size after tempering.
Table 8 below lists the mechanical property of YB5B.
Table 8：YB5B mechanical property：
Conclusion：Hardening heat 1020-1060 DEG C, is tempered 550-600 DEG C.
Table 9 below lists the mechanical property of YB5C.
Table 9：YB5C mechanical property
200*300 one-heating forming in table, heating is short for diffusion time, and lateral performance is poor, needs two fire diffusions, repeatedly upsetting pull.
Table 10：Results of property after YB5C High temperature diffusion
Conclusion：Hardening heat 1020-1060 DEG C, is tempered 560-600 DEG C.
Embodiment 5
High temperature alloy mould diskware is prepared with embodiment 2YB5B steel heat treatment, be labeled as JBD275-YB5B- φ
900x300.Process of thermal treatment condition is with embodiment 4.
Embodiment 6
High temperature alloy mould diskware is prepared with embodiment 3YB5C steel heat treatment, be labeled as JBD275-YB5C- φ
900x300.Process of thermal treatment condition is with embodiment 4.
Embodiment 7
Blade steel mold is prepared with the YB5A steel heat treatment of embodiment 1, be labeled as SM985RL.DJ-YB5A-
1700x700x420 module.Technology for Heating Processing is as follows：
S1 quenches：≤ 650 DEG C of shove charges, are warming up to 820 DEG C × (6 ± 0.5) h with stove by 650 DEG C × (4 ± 0.5) h isothermal, with
Stove be warming up to 1010 DEG C × (9 ± 0.5) h, 120～130min of oil cooling, fuel-displaced (in the air stop less than half an hour) immediately is returned
Fire；
S2 is once tempered：≤ 280 DEG C of shove charges, are warming up to 580～590 DEG C × (20 ± 0.5) h by 280 DEG C × (7 ± 0.5) h
Oil cooling is cooled to air cooling after 100～150 DEG C of surface temperature, during fuel-displaced air cooling, it is ensured that mould can just carry out second after being cooled to room temperature
Tempering；
S3 double tempering：≤ 580 DEG C enter stove, and 580 DEG C × (18 ± 0.5) h is air cooled to less than 100 DEG C and can just carry out third time
Tempering；
Tri- tempering of S4：≤ 580 DEG C enter stove, 580 DEG C × (16 ± 0.5) h air cooling is cooled to room temperature carries out Rockwell hardness inspection
Survey；
Blade Steel die hardness is required：Case hardness is maximum no more than 48HRC, and minimum cannot be below 38HRC.
Embodiment 8
High temperature alloy mould is prepared with the YB5B steel heat treatment of embodiment 2, be labeled as SM985RL.DJ-YB5B-1700 ×
700 × 420 modules.Process of thermal treatment condition is with embodiment 7.
Embodiment 9
High temperature alloy mould is prepared with the YB5C steel heat treatment of embodiment 3, be labeled as SM985RL.DJ-YB5C-1700 ×
700 × 420 modules.Process of thermal treatment condition is with embodiment 7.
Test example
1) performance test
Hardness balance under YB5A temperature different from H13, sees Fig. 1.
The anti-temper resistance of YB5A, YB5B, YB5C and H13 is relatively shown in Table 11.
Table 11：H13, YB5A, YB5B temperature and hardness relation
Note:It is 565 DEG C, 585 DEG C, 610 DEG C respectively that YB5C corresponds to hardness HRC53,49～50,45 temperature.(it is shown in Table
9～10)
It can be seen that the anti-temper resistance of YB5A, YB5B and H13 is same level, the anti-temper resistance of YB5C is then higher.
2) deflection compares, and compares the result that existing four kinds of mould steel forges high temperature alloy diskware in following table, it is seen that
5CrNiMo, 5CrNiMoV, import FX make a call to 4 deflections more than 4mm, H13 crack of die.
12 deflection of table compares
Table 13 beats 8 deflection comparing results of cake part for YB5A mould with 5CrNiMoV build-up welding mould.Respectively test on mould
Fig. 2 is seen in the position of point.Wherein 2A-1～2A-4 is YB5A result, and it is built-up welding to deform less than 1mm, 2A-5～2A-8 for 5CrNoMoV
Result, deform maximum 3.5mm.
Before and after table 14 forges high temperature alloy cake part use for YB5A mould, hardness data is contrasted.It can be seen that mould hardness drop on YB5A
Low about 2～3 HRC, 5～8 HRC drop in lower mould.Built-up welding upper and lower mould hardness all reduces about 2～3 HRC, less than YB5A.YB5A mould
Tool deforms less than 1mm, built-up welding 5CrNiMoV deformation 3.5mm, it is seen that YB5A mould bulk strength height is little main of die deformation
Reason.
YB5B mould and YB5C mould diskware prepared by embodiment 5 and embodiment 6, use through client, it was demonstrated that its performance phase
When or be better than H13 mould steel, and H13 is not suitable for relatively large forging die.YB5B mould and YB5C mould are proved to fully meet relatively
The requirement of large-scale and greater impact power.
Table 13
Table 14
4) YB5A mould is in the JBD275 high temperature alloy disk life-span
Five～eight grades of disk moulds that YB5A material makes produce JBD275 altogether and amount to 58 (without false material).On first time
The continuous die forging 4 in field, repetition measurement die deformation ＜ 0.2mm after end, does not do reparation and is continuing with；Enter the court for the second time continuous die forging 19
Part, repetition measurement die deformation ＜ 0.9mm after end, does not do reparation and is continuing with；Third time is entered the court continuous die forging 35, multiple after end
Survey die deformation ＜ 1.0mm.
Mould repetition measurement data after three ends, it is seen that plasticity when YB5A mold materials forge solid high temperature alloy disk
Deformation is less, and surface abrasion is less.It is thus regarded that YB5A mold materials can be competent at the forging of solid diskware under prevailing conditions
Production.
5) application result of the YB5A mould on stainless steel blade forging
SM985RL.DJ-YB5A lower mould is entered the court front surface 42～44HRC of hardness, and end hardness is basically unchanged.Finish-forging
Mould size comparison, production quantity 120 (SPKA11200), blade mould maximum distortion 0.3mm, blade root mould maximum are descended in front and back
Deformation 0.5mm, the essentially unchanged shape of mould.Lower mould size comparison, production quantity before and after SM985RL.DJ-5CrNiMoV mould finish-forging
20 (SPKA22400), mould enter the court before 44～48HRC of hardness, mould maximum distortion 1.565mm, deform larger.
From the angle of project, solve the problems, such as that high alloy hammering mould can be used in 3.55 ten thousand tons of fly presses, really
Having determined YB5A mould can be used for the forging of 3.55 ten thousand tons of Blade Steels.
6) result that YB5A, YB5B, YB5C are applied on other hot forged moulds
For spindle hot-forging die service life 15000, it is three times of 5CrNiMo.For vapour bent axle hot-forging die
Advantage is not ftracture, and the life-span is suitable with H13.Application major advantage on other hot-forging dies is indeformable, forging surface size
High precision, without reconditioning.
The disclosed above or embodiment that requires less than can make in the range of existing disclosed laboratory facilities or
Implement.All of product and/or method described by the preferred embodiment of the present invention, expressly refers to that those do not violate the present invention
Concept, scope and spirit can be used for the product and/or experimental technique and following step.To in described technique
The all of change of technological means and improvement, belong to concept, the scope and spirit of the claims in the present invention definition.
Claims (10)
1. a kind of Cr5 series hot die steel, it is characterised in that the hot die steel in terms of weight %, comprising C0.40～
0.48%, Si 0.20～1.2%, Mn 0.40～0.80%, P≤0.020%, S≤0.010%, Cr4.80～5.50%, Ni 1.40
～2.0%, Mo0.80～1.50%, V0.50～0.70%, W0.50-1.00%, Co 0～0.75%, Al0.01～0.20%,
Nb0.02～0.20%, the Fe of surplus；
The preparation method of the Cr5 series hot die steel, including step：
Electric furnace or converter smelting, LF stove refine, vacuum outgass, molding, annealing, electroslag remelting, slow cooling, annealing, forging, normalizing,
Spheroidizing, expansion hydrogen, slightly add, inspection, slightly add, quenched, finishing, check.
2. the hot die steel according to claim, it is characterised in that the hot die steel in terms of weight %, comprising C
0.40～0.48%, Si 0.20～0.40%, Mn0.40～0.80%, P≤0.020%, S≤0.010%, Cr4.80～5.50%,
Ni1.40～2.0%, Mo0.80～1.50%, V0.50～0.70%, W0.50-1.00%, Al0.06～0.20%, Nb0.02～
0.20%, the Fe of surplus.
3. the hot die steel according to claim, it is characterised in that the hot die steel in terms of weight %, comprising
C0.40～0.48%, Si 0.4～1.0%, Mn 0.40～0.80%, P≤0.020%, S≤0.010%, Cr4.80～5.50%,
Ni1.40～2.0%, Mo0.80～1.50%, V0.50～0.70%, W0.50-1.00%, Al0.01～0.04%, Nb0.02～
0.20%, the ferrum of surplus.
4. the hot die steel according to claim, it is characterised in that the hot die steel in terms of weight %, comprising
C0.40～0.48%, Si 0.20～0.40%, Mn0.40～0.80%, P≤0.020%, S≤0.010%, Cr4.80～5.50%,
Ni1.40～2.0%, Mo0.80～1.50%, V0.50～0.70%, W0.50-1.00%, Co 0.50～0.75.%, Al0.06～
0.20%, Nb0.02～0.20%, the ferrum of surplus.
5. a kind of preparation method of alloy mold, the alloy mold is high temperature alloy mould, blade steel mold and low-alloy steel
One kind in mould, it is characterised in that with the hot-work die steel making described in any one of Claims 1 to 4, including step：
S1 quenches：≤ 650 DEG C of shove charges, isothermal at a temperature of being maintained at 650 DEG C, 800～820 DEG C of isothermals are warming up to stove, during isothermal
Between calculate by effective dimensions 0.6min/mm of workpiece, then be warming up to 1000～1020 DEG C with stove, kept for 10～12 hours, oil cooling
Be cooled to 150～180 DEG C fuel-displaced after be tempered immediately；
S2 is once tempered：≤ 280 DEG C of shove charges, 4～10h of isothermal at a temperature of being maintained at 280 DEG C, 570～595 DEG C are warming up to, are kept
14～22h, oil cooling is cooled to air cooling after 100～150 DEG C of surface temperature, during fuel-displaced air cooling, it is ensured that mould can just enter after being cooled to room temperature
Row is tempered for second；
S3 double tempering：≤ 300 DEG C enter stove, 560 DEG C of holding 12h of diskware, or 580 DEG C of holding 18h of blade, be air cooled to 100 DEG C with
Under.
6. preparation method according to claim 5, it is characterised in that the alloy mold is high temperature alloy mould or blade
Steel mold, its preparation method includes
Tri- tempering of S4：≤ 300 DEG C enter stove, and 580 DEG C of temperature keep 1.8min/mm, and air cooling is cooled to room temperature carries out Rockwell hardness inspection
Survey.
7. preparation method according to claim 5, it is characterised in that
In step sl, isothermal 0.6min/mm at a temperature of being maintained at 650 DEG C, is warming up to 800～820 DEG C of holding 0.6min/ with stove
Mm, then with stove be warming up to 1000～1020 DEG C holding 1.0～1.2min/mm, be cooled to 150～180 DEG C fuel-displaced after be tempered immediately；
In step s 2, diskware keeps diskware 15h in 570～580 DEG C of temperature, or blade keeps 21h in 585-595 DEG C of temperature,
Oil cooling is cooled to air cooling after 100～150 DEG C of surface temperature, during fuel-displaced air cooling, it is ensured that mould can just carry out S3's after being cooled to room temperature
Double tempering；
In step s3,560 DEG C of temperature of diskware keep diskware 12h, or blade keeps 18h at 580 DEG C, is air cooled to less than 100 DEG C
Carry out third time tempering；
In step s 4,560 DEG C of temperature of diskware keep 10h, or 580 DEG C of holding 16h of blade.
8. preparation method according to claim 5, it is characterised in that
In step sl, isothermal 0.6min/mm at a temperature of being maintained at 650 DEG C, is warming up to 820 DEG C of holding 0.6min/mm with stove, then
With stove be warming up to 1000～1020 DEG C holding 1.0～1.2min, be cooled to 150～180 DEG C fuel-displaced after be tempered immediately；
In step s 2, in 585～595 DEG C of temperature, 2.4～3.0min/mm is kept, oil cooling is cooled to 100～150 DEG C of surface temperature
Air cooling afterwards, during fuel-displaced air cooling, it is ensured that mould carries out the double tempering of S3 after being cooled to room temperature；
In step s3,580 DEG C of temperature keep 1.8～2.4min/mm, and being air cooled to less than 100 DEG C carries out third time tempering.
9. the preparation method according to any one of claim 5～8, it is characterised in that the final step air cooling of preparation method
After being cooled to room temperature, Rockwell hardness detection is carried out, the hardness requirement for high temperature alloy mould is：Case hardness is maximum no more than
52HRC, minimum cannot be below 42HRC；To blade steel mold and the hardness requirement for closing knot steel mold it is：Case hardness maximum can not
More than 48HRC, minimum cannot be below 38HRC.
10. with mould obtained in the arbitrary described preparation method of claim 5～9.
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