CN105950969A - High-heat-resistant austenite die steel and preparation method thereof - Google Patents
High-heat-resistant austenite die steel and preparation method thereof Download PDFInfo
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- CN105950969A CN105950969A CN201610289982.XA CN201610289982A CN105950969A CN 105950969 A CN105950969 A CN 105950969A CN 201610289982 A CN201610289982 A CN 201610289982A CN 105950969 A CN105950969 A CN 105950969A
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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
- 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
- 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
- C22C38/12—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
- C21D2211/001—Austenite
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Abstract
The invention provides high-heat-resistant austenite die steel and a preparation method thereof. The die steel comprises, by weight, 0.61%-0.79% of C, 1.20%-1.40% of Si, 12.5%-15.0% of Mn, 6.5%-7.0% of Cr, 1.0%-3.0% of Mo, 1.0%-2.0% of V, no more than 0.02% of P, no more than 0.005% of S, and the balance Fe and inevitable impurities; and the formula that C=0.025*Mn+0.03*Cr+0.10*V is met. The problems that martensite hot work die steel is not sufficient in strength and hardness at the high temperature of 680 DEG C are solved, and according to the heat resistance indexes of the prepared austenite hot work die steel under the 650 DEG C heat preservation condition, the Rockwell hardness is HRC45 or above after continuous heat preservation of 2.5 h at the temperature of 650 DEG C, and the Rockwell hardness is HRC45 or above after continuous heat preservation of 5.0 h at the temperature of 650 DEG C. Compared with the traditional martensite 3Cr2W8V hot work die steel, the heat resistance of the austenite die steel is improved by 50% or above, and the austenite die steel is suitable for manufacturing of high-temperature alloy extrusion dies and can replace the universal martensite hot work die steel at the working temperature of 680 DEG C.
Description
Technical field
The present invention relates to hot die steel, be specifically related to a kind of high heat-resisting austenite mould steel and preparation thereof
Method, particularly relates to a kind of heat still under 680 DEG C of operating temperatures with elevated temperature strength and high temperature hardness
Make mould steel and preparation method thereof.
Background technology
High refractory steel belongs to the material category of hot die steel, and hot die steel is to add for manufacture
Heat is to metal more than recrystallization temperature or the die steel of liquid metal molding.Such mould steel is main
For manufacturing hammer forging die, forcing press forging die, hot extruding die and compression mod, the most both by relatively favourable opposition
The effect hitting load is acted on by rapid heat cycle or high temperature again, so that the working condition of mould is complicated
Change, badly change.And mould operationally contacts with thermometal, cavity surface can be heated and is warming up to
300～400 DEG C (hot-forging die), 500～800 DEG C (hot extruding die).Therefore, hot die steel should have
There are enough elevated temperature strengths and hardness.
At present, on domestic and international mold materials market, most widely used hot-work die steel material is martensite
Steel, such as 3Cr2W8V (composition quality percent is: C:0.30～0.40%, Si 0.40%,
Mn 0.40%, Cr:2.20～2.70%, W:7.50～9.00, V:0.20～0.50%, P 0.030%,
S 0.030%), their Technology for Heating Processing is tempering type of quenching, and its tempered structure of quenching is tempered martensite
The carbide reinforced phase of the disperse of distribution on body+matrix, when temperature reaches 650 DEG C, they all can not
Occurring with avoiding to reply to soften, tempered martensite matrix decomposes, carbide agglomeration, and matrix softens,
Cause material failure.
Traditional hot die steel 3Cr2W8V steel uses electric furnace steel making, forging to become a useful person, Tempering and Quenching
The technique manufacture of (quenching+tempering), Technology for Heating Processing uses 1050～1070 DEG C to quench+550～570 DEG C
Tempering, the heat resistance index of its key is: 650 DEG C of Rockwell hardness HRC30 being persistently incubated after 2.5h；
650 DEG C of Rockwell hardness HRC25 being persistently incubated after 5.0h.The most persistently military service can cause being tempered horse
Family name soma decomposes and the agglomeration of tiny carbide, causes the absent-mindedness of grain boundaries adhesion to be drawn
Playing the ultimate failure of material, the hot-work die that such martensite die steel material manufactures should at 680 DEG C
During with, service life will be very limited.
Chinese patent CN1924069A discloses the quenched high heat-intensity hot-work die steel of martensite type
Material, the span of control of its chemical composition is: Cr:3.5～4.0%, Mo:2.0～2.5%, V:1.0～1.5%,
W:1.0～1.5%, Mn:0.1～0.5%, Ni:0.1～0.25%, C:0.3～0.35%, Si:0.1～0.5%,
S:0.005～0.01%, P:0.01～0.02%, surplus is Fe；The mechanism of its strengthening is mainly passed through
Martensitic phase transformation, and obtain the invigoration effect of tempered sorbite tissue and alloy carbide to reach high-strength
The effect of toughness, but the temperature of this martensite type hot die steel the highest heat resistanceheat resistant intensity is difficult to surpass
Cross 610 DEG C, if material military service temperature reaches 680 DEG C, it may occur that the hot mastication behavior of material, material
Intensity and the hardness of material drastically decline, and cause the inefficacy of material.
United States Patent (USP) US2010/0193089 discloses the high epistasis hot-work die of a kind of high-carbon height tungsten type
Steel material, the span of control of its chemical composition is: C:0.34～0.40%, Cr:4.9～5.5%, Si:
0.3～0.5%, Mn:0.45～0.75%, V:0.5～0.7%, (Mo+l/2W) 2.5-2.9%, Ni < 0.5%；
Mainly increased the precipitation strength of category of carbides by raising carbon content and chromium, tungsten content, reach
The elevated temperature strength of reinforcing material and hardness, but essentially, this material falls within martensite
Type high heat-intensity hot-work die steel, its highest service temperature is not easy to more than 600 DEG C, if exceeding
This temperature can occur the gathering of carbide and grow up, and causes the high temperature hardness of material after invigoration effect exhaustion
Decline.
Summary of the invention
It is an object of the invention to provide a kind of high heat-resisting austenite mould steel and preparation method thereof, solve
Existing martensite hot die steel is elevated temperature strength and the technical problem of hardness deficiency at 680 DEG C, promotes
Hot die steel heat resistance under 680 DEG C of high temperature operating conditions, it is adaptable to the die casting of copper alloy,
The hot extrusion shaping mold of the high heat-intensity materials such as heat-resisting alloy, high temperature alloy, corronil, and
The manufacture of titanium alloy creep forming mould.
For reaching above-mentioned purpose, the technical scheme is that
The present invention use the relatively low manganese element of price as the main alloy element in material alloys composition,
Material is made to obtain stable austenite structure matrix, and in the solution strengthening of alloying element and precipitation strength
Compound action be issued to having high hot strength performance.And it is possible to improve manufacturing cost further so that material
Material manufactures more economically, improves the product competitiveness of manufacturing enterprise.
A kind of high heat-resisting austenite mould steel, its chemical component weight percentage ratio is: C:0.61～0.79%,
Si:1.20～1.40%, Mn:12.5～15.0%, Cr:6.5～7.0%, Mo:1.0～3.0%, V:
1.0～2.0%, P≤0.02%, S≤0.005%, remaining is Fe and inevitable impurity, and above-mentioned unit
Element need to meet following relation: C=0.025Mn+0.03Cr+0.10V simultaneously.
Further, the microstructure of described height heat-resisting austenite mould steel is single austenite structure.
Height of the present invention heat-resisting austenite mould steel Rockwell hardness after 650 DEG C persistently insulation 2.5h
For more than HRC45；650 DEG C of Rockwell hardness being persistently incubated after 5.0h are more than HRC45.
In the composition of steel of the present invention designs:
Carbon: carbon is the element expanding austenite region, when carbon content increases, can suitably reduce manganese
Content, thus alleviate the flow harden phenomenon of steel.Meanwhile, the raising of carbon content, can improve base
The intensity of body, it is possible to form different carbides with other alloying elements, reaches to strengthen the effect of matrix
Really.But, when carbon content is too high, the toughness of steel will be adversely affected, and reduces the cold-and-heat resistent of steel
Fatigue behaviour.Therefore, the present invention controls carbon content is 0.61～0.79%.
Silicon: silicon is that the affinity of one of element common in steel, silicon and oxygen is only second to aluminum and titanium, and strong
Yu Meng, chromium, vanadium, so in steelmaking process, silicon is used as reducing agent and deoxidizer.Silicon in steel not
Forming carbide, but be present in austenite with the form of solid solution, it improves solid solution in steel
The effect of intensity and cold deformation hardening ratio is extremely strong, is only second to phosphorus.In order to deoxidation is good, potassium steel
Middle silicone content should be not less than 1.20%.The material impact toughness that causes for preventing silicone content too low and resistance to
The decline of mill property, it is proposed that its content controls 1.20～1.40%.Additionally, silicon is conducive to carbide at height
Separate out during warm hardening, it is also possible to increase the spread of carbide precipitate, improve high-temperature oxidation resistant energy
Power and matrix drag.Therefore, the present invention controls silicone content is 1.20～1.40%.
Manganese: manganese is the basic element forming austenite in steel of the present invention, and therefore, Fe content is greatly improved,
Make the expansion that the austenite phase of material is enough, so can make material tissue after high temperature cooling still
It is so austenite structure, it is thus achieved that the phase of single austenite structure, constitutes the most micro-group of the present invention
Knit.But the Fe content upper limit to be controlled, because there is flow harden phenomenon in potassium steel, when its content mistake
Gao Shi, is unfavorable for machining.Therefore, in the range of the content of manganese to be selected in reasonably, the present invention controls
Fe content is 12.5～15.0%.
Chromium: chromium adds machinability and the antioxygenic property that can significantly improve steel in steel, increases steel
Resistance to corrosion.Chromium also can dissolve in austenite, plays solution strengthening effect, in the cooling procedure of material
The corresponding alloy carbide of middle precipitation plays invigoration effect.It addition, chromium can be formed stably with coordinating of manganese
Austenite, therefore can reduce the addition of manganese.It is 6.5～7.0% that the present invention controls chromium content.
Molybdenum: molybdenum belongs to the element reducing austenite phase field, molybdenum is present in solid solution phase and carbonization in steel
In thing.In Carbide Phases, when molybdenum content is relatively low, form compound cementite with ferrum and carbon；When
When molybdenum content is higher, then form the alloy carbide of its own.The diffusion velocity of molybdenum is much smaller than the expansion of carbon
Dissipate speed.Molybdenum effect in steel can be summarized as improving quenching degree, improving heat resistance, prevent Temper brittleness
Property, improve remanent magnetism and coercivity, improve corrosion stability in some medium and prevent spot corrosion tendency etc..
In austenitic steel, molybdenum dissolves in austenite, solution strengthening matrix, it is also possible to form carbide, increases
The strong elevated temperature strength of steel, hardness and wearability.When the content of molybdenum is more than 3%, easily cause steel
Decarburization, its content conservative control to be obtained, it is 1.0～3.0% that the present invention controls molybdenum content.
Vanadium: vanadium is one of reinforced ferrite and austenite phase field formation element, and it is with carbon, nitrogen, oxygen all
There is extremely strong affinity, form the most stable compound therewith.In steel, vanadium is mainly with carbon
The form of compound exists.Its Main Function in steel is: the tissue of refinement steel and crystal grain, improves crystalline substance
Grain Coarsening Temperature, thus reduce the superheated susceptivity of steel, and improve intensity and the toughness of steel；Increase steel
Temper resistance.
In Austenitic Hot Work Die Steel, act primarily as invigoration effect is the carbide of vanadium, and vanadium is strong carbon
Compound forms element, in ag(e)ing process, by the combination of vanadium Yu carbon, the substantial amounts of VC of disperse educt,
Strengthening matrix.The microhardness (HV) of vanadium carbide reaches 2500～2800, after its content exceedes certain value,
Will harden because coherence separates out alloy carbide.Vanadium is in Austenitic Hot Work Die Steel, it is also possible to thin
Change austenite crystal, increase intensity and the toughness of steel, improve the wearability of steel.Consider, this
Bright control content of vanadium is 1.0～2.0%.
Phosphorus: phosphorus is very harmful element in potassium steel, its dissolubility in molten steel is extremely low, and often
Occur on crystal boundary with phosphide thin film, make foundry goods be prone to crack, particularly during carbon content height,
More exacerbate this hazardness of phosphorus.
Sulfur: it is generally acknowledged that sulfur is to remain in one of harmful element in steel, so specifying in high-quality steel
Its content cannot be greater than 0.04%, even if in common straightcarbon steel, also limits and cannot be greater than 0.055%.
For austenitic steel, in steel, p and s forms phosphide and sulfide at Ovshinsky in process of setting
Body grain boundary precipitate, thus produce intercrystalline britftleness, makes the plasticity of steel reduce, when also can make steel ingot forging rolling
Line of segragation cracks, and reduces the mechanical property of steel.Therefore, the present invention controls P≤0.020%,
S≤0.005%.
Chemical composition of the present invention also needs to meet relationship:
C=0.025Mn+0.03Cr+0.10V.Because Mn is that austenite structure forms element in the present invention,
Stable austenite structure could be formed when meeting above-mentioned relation with C, and Cr and V is all strong carbonization
Thing forms element, and the microscopic structure of steel just can be made when C meets above-mentioned relation to obtain tiny alloy carbon
Compound is distributed in austenitic matrix tissue, and strengthening matrix also can be greatly improved thermal stability.
The preparation method of height of the present invention heat-resisting austenite mould steel, it comprises the steps:
1) smelt
According to above-mentioned chemical composition, use induction furnace to carry out melting, be cast into steel ingot afterwards, then carry out
Electroslag remelting；
2) forging
Steel ingot enters heating furnace heating, and steel ingot charging temperature is 500～600 DEG C, with the liter of 80～100 DEG C/h
Temperature speed is heated to 1210～1250 DEG C, is incubated 2～4 hours；Carry out forging processing, initial forging temperature again
It is 1080～1130 DEG C, final forging temperature >=900 DEG C；
3) heat treatment
Solution treatment+Ageing Treatment, wherein, solid solubility temperature is 1050～1220 DEG C, and aging temp is
650～780 DEG C.
Further, the microstructure of described high refractory steel is single austenite structure.
The high refractory steel of the present invention Rockwell hardness HRC45 after 650 DEG C persistently insulation 2.5h
Above；650 DEG C of more than Rockwell hardness HRC45 being persistently incubated after 5.0h.
The main technologic parameters of the present invention controls as follows:
Step 2 of the present invention) steel ingot is heated to the programming rate of 80～100 DEG C/h in heating furnace
It is incubated 2～4 hours: in heating process, the thermal stress sensitivity of steel ingot is higher after 1210～1250 DEG C,
Easily producing stress cracking, the charging temperature of steel ingot is controlled at 500～600 DEG C by the present invention, and heat up speed
Degree controls to be possible to prevent steel ingot to produce crack due to thermal stress in heating process at 80～100 DEG C/h；In heating
It is incubated 2～4 hours so that the temperature on the whole surface of steel ingot to core all may be used after 1210～1250 DEG C
Keep uniformly, the malleability of steel ingot to be improved, preventing steel tearing tendency in forging process, and
Improve the microscopic structure of steel and the uniformity of alloying component, improve intensity and the toughness of steel.
Initial forging temperature through diameter forging machine hammer cogging is 1080～1130 DEG C: owing to steel of the present invention exists
It is austenite one phase tissue regions in the range of 1080～1130 DEG C, has optimal high temperature thermoplasticity, have
It is beneficial to high temperature deformation processed, it is not easy to produce high-temperature hot processing cracking.
Diameter forging machine final forging temperature >=900 DEG C during controlled forge process of the present invention: due to steel ingot final forging temperature pair
Steel ingot forging quality has important impact, and final forging temperature is less than 900 DEG C, causes material plasticity to decline,
It is very easy to cause steel ingot to produce ingot cracking in diameter forging machine forging process.
Heat treatment solid solubility temperature is controlled at 1050～1220 DEG C by the present invention, and aging temp controls
650～780 DEG C: under 1050～1220 DEG C of temperature ranges, the Ovshinsky tissue of Steel material of the present invention can promote
Make alloying element dissolve in matrix in a large number, improve alloy degree, strengthen solid solution strengthening effect.Meanwhile, entering
During row Ageing Treatment 650～780 DEG C, the second phase particles that disperse educt is tiny is strong by precipitation
Change and improve the strength of materials and hardness.
The heat-resisting Austenitic Hot Work Die Steel of height of the present invention select manganese as stable austenite element,
In potassium steel, the amount of precipitation of carbide is more, and the dissolubility of carbide own is higher, and dissolution velocity is relatively slow,
After precipitation, at high temperature long-time heating shows good stability and slower coarsening rate, is conducive to
The elevated temperature strength of material；Additionally, manganese is as stable alloy element, its price is relatively low, has substantially
Cost advantage, in rapid economic development, the current era of energy scarcity, there is far reaching significance.
It is thin that the present invention uses in the carbide solution strengthening in single phase austenite tissue and ag(e)ing process
The compound action of little Carbide Precipitation strengthening reaches the high heat-intensity of material, is belonging to non-martensite phase transformation
Material, no matter the Austenitic Hot Work Die Steel prepared is under room temperature or high temperature operating conditions, matrix
Remain austenitic state, the reply producing martensite steel can be avoided to soften problem.This Ovshinsky body heat
Make the strengthening mechanism that the service temperature of mould steel can reach under more than 680 DEG C, high temperature to have with prior art
Difference substantially.
Beneficial effects of the present invention:
For martensite hot die steel elevated temperature strength and problem of hardness deficiency at 680 DEG C, this
Bright steel chooses the relatively low manganese element of price as major stable austenitic alloy element, with chromium, molybdenum, vanadium
Alloying element forms alloying element as main matrix solution strengthening element and diffusion-precipitation hardening constituent,
The high heat-intensity Austenitic Hot Work Die Steel prepared has good thermally-stabilised at a temperature of 680 DEG C
Performance, this steel crucial heat resistance index under 650 DEG C of heat-retaining conditions is: 650 DEG C are persistently incubated 2.5h
After Rockwell hardness at more than HRC45；650 DEG C of Rockwell hardness being persistently incubated after 5.0h are at HRC45
Above, compared with traditional martensite 3Cr2W8V hot die steel, the thermostrength of steel of the present invention
Promote more than 50%.
The die steel heat treatment deformation of present invention exploitation is little, and price is low, has higher high-temperature hot
Epistasis energy, it is adaptable to manufacture high temperature alloy extrusion die, can replace general under 680 DEG C of operating temperatures
Martensite hot die steel.
Accompanying drawing explanation
Fig. 1 is the embodiment of the present invention 7 steel typical metallograph after solid solution is incubated.
Fig. 2 is the embodiment of the present invention 7 steel typical metallograph after solid solution+timeliness insulation.
Fig. 3 is the embodiment of the present invention 7 steel with 3Cr2W8V steel at 650 DEG C of heat preservation hot stabilities pair
Ratio.
Detailed description of the invention
Below in conjunction with embodiment and accompanying drawing, the present invention will be further described.
Table 1 is the composition of embodiment of the present invention steel, and table 2 is the preparation technology ginseng of embodiment of the present invention steel
Number, table 3 is the high-temperature heat-resistance performance index of embodiment of the present invention steel.
Embodiment of the present invention manufacturing process is as follows:
According to the chemical composition in table 1, use induction furnace to carry out melting, be cast into steel ingot afterwards, water
The steel ingot cast will be positioned in electroslag remelting device as consutrode, carry out electroslag remelting, liquid
Metal falls in following water mold through the slag blanket of slag bath, is more again frozen into 1.0～1.5
Ton steel ingot；Again the steel ingot solidified enters heating furnace heating, and steel ingot charging temperature is 500～600 DEG C,
In heating furnace, it is heated to 1210～1250 DEG C with the programming rate of 80～100 DEG C/h, is incubated 2～4 hours；
Forging processing, initial forging temperature 1080～1130 DEG C, final forging temperature >=900 DEG C are carried out after insulation.At Re
Reason solid solubility temperature controls at 1050～1220 DEG C, and aging temp controls at 650～780 DEG C, concrete technology
Parameter sees table 2.
Austenitic Hot Work Die Steel prepared by the detection embodiment of the present invention is after 650 DEG C persistently insulation 2.5h
Rockwell hardness；650 DEG C of Rockwell hardness being persistently incubated after 5.0h, concrete testing result sees table 3.
Fig. 1 is the embodiment of the present invention 7 steel typical metallograph after 1170 DEG C of solid solution insulations.By scheming
1 understands, and in steel, major part carbide all dissolves in austenitic matrix and plays solution strengthening effect, but still
Having a small amount of undissolved carbide, size is about 5 μm, and these carbides are most on matrix, on crystal boundary
Less.Owing to these carbides are pinned on austenitic matrix, can stop austenite during solid solution
Grow up, improve steel toughness.
Fig. 2 is that the embodiment of the present invention 7 steel is after 1170 DEG C of solid solutions and 700 DEG C of timeliness are incubated 4 hours
Typical metallograph.As shown in Figure 2, after timeliness, autstenitic grain size is not changed in substantially, i.e. exists
In ag(e)ing process, austenite is not grown up, and has a large amount of tiny precipitated phase forming core after timeliness to separate out in addition,
Dispersed precipitate on matrix, notable strengthening material performance.
As shown in Table 3, the steel that prepared by present invention Rockwell hardness after 650 DEG C persistently insulation 2.5h exists
More than HRC45；650 DEG C of Rockwell hardness being persistently incubated after 5.0h, at more than HRC45, have excellent
Good thermal stability.Visible, the invention provides one and have under the conditions of 680 DEG C of applied at elevated temperatures
The Austenitic Hot Work Die Steel material of good elevated temperature strength.
For elevated temperature strength, hot die steel main performance index operationally is presented as material under high temperature
The anti-softening ability of material, therefore, the present invention selects the number that the hardness under hot conditions changes over time
Reflect its high temperature resistance softening power according to index, evaluate the quality of its heat resistance with this.
Fig. 3 be the embodiment of the present invention 7 steel after Technology for Heating Processing is 700 DEG C of timeliness of 1170 DEG C of solid solutions
650 DEG C of thermal stabilities and 3Cr2W8V are thermally-stabilised at 650 DEG C after+560 DEG C of tempering of 1050 DEG C of quenchings
The contrast of performance.From the figure 3, it may be seen that steel of the present invention is in 650 DEG C of insulating processes, hardness stabilization exists
More than 45HRC, and 3Cr2W8V is with holding time, hardness downward trend is obvious, the most firmly
Degree only about 20HRC, cannot meet the performance requirement of mold work completely.
Table 1 unit: wt%
| C | Si | Mn | Cr | Mo | V | P | S | |
| Embodiment 1 | 0.75 | 1.20 | 14.79 | 6.53 | 1.78 | 1.89 | 0.016 | 0.003 |
| Embodiment 2 | 0.61 | 1.22 | 12.50 | 6.50 | 3.00 | 1.00 | 0.011 | 0.003 |
| Embodiment 3 | 0.70 | 1.31 | 12.90 | 7.00 | 2.06 | 1.67 | 0.012 | 0.005 |
| Embodiment 4 | 0.68 | 1.20 | 14.10 | 6.89 | 1.00 | 1.23 | 0.011 | 0.001 |
| Embodiment 5 | 0.79 | 1.40 | 15.00 | 7.00 | 1.59 | 2.00 | 0.020 | 0.003 |
| Embodiment 6 | 0.69 | 1.33 | 13.30 | 6.80 | 2.68 | 1.55 | 0.016 | 0.003 |
| Embodiment 7 | 0.71 | 1.25 | 13.70 | 6.90 | 2.50 | 1.70 | 0.011 | 0.003 |
Table 2
Table 3
Claims (6)
1. a high heat-resisting austenite mould steel, its chemical component weight percentage ratio is: C:0.61～0.79%,
Si:1.20～1.40%, Mn:12.5～15.0%, Cr:6.5～7.0%, Mo:1.0～3.0%, V:
1.0～2.0%, P≤0.02%, S≤0.005%, remaining is Fe and inevitable impurity, and on
State element and need to meet following relation: C=0.025Mn+0.03Cr+0.10V simultaneously.
Height the most according to claim 1 heat-resisting austenite mould steel, it is characterised in that described height is resistance to
The microstructure of hot austenite mould steel is single austenite structure.
Height the most according to claim 1 and 2 heat-resisting austenite mould steel, it is characterised in that described
High heat-resisting austenite mould steel Rockwell hardness after 650 DEG C persistently insulation 2.5h HRC45 with
On；650 DEG C of Rockwell hardness being persistently incubated after 5.0h are at more than HRC45.
4. the preparation method of high heat-resisting austenite mould steel as described in any one of claim 1-3, it include as
Lower step:
1) smelt
Use induction furnace to carry out melting according to chemical composition described in claim 1, be cast into steel afterwards
Ingot, then carry out electroslag remelting；
2) forging
Steel ingot enters heating furnace heating, and steel ingot charging temperature is 500～600 DEG C, with 80～100 DEG C/h's
Programming rate is heated to 1210～1250 DEG C, is incubated 2～4 hours；Carry out forging processing again,
Initial forging temperature is 1080～1130 DEG C, final forging temperature >=900 DEG C；
3) heat treatment
Solution treatment+Ageing Treatment, wherein, solid solubility temperature is 1050～1220 DEG C, and aging temp is
650～780 DEG C.
The preparation method of height the most according to claim 4 heat-resisting austenite mould steel, it is characterised in that
The microstructure of described height heat-resisting austenite mould steel is single austenite structure.
6. according to the preparation method of the heat-resisting austenite mould steel of the height described in claim 4 or 5, its feature
It is, described height heat-resisting austenite mould steel Rockwell hardness after 650 DEG C persistently insulation 2.5h
At more than HRC45；650 DEG C of Rockwell hardness being persistently incubated after 5.0h are at more than HRC45.
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