CN108531821A - One kind extrusion die steel containing aluminothermy and its production method - Google Patents
One kind extrusion die steel containing aluminothermy and its production method Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22B—PRODUCTION AND REFINING OF METALS; PRETREATMENT OF RAW MATERIALS
- C22B9/00—General processes of refining or remelting of metals; Apparatus for electroslag or arc remelting of metals
- C22B9/16—Remelting metals
- C22B9/18—Electroslag remelting
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
- C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
- C23C8/24—Nitriding
- C23C8/26—Nitriding of ferrous surfaces
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/25—Process efficiency
Abstract
The present invention relates to a kind of extrusion die steel containing aluminothermy and its production method, which improves C content on the basis of H13 steel, reduces Si, Cr, Mo content, alloy total content ratio H13 few about 2.5~3.5%, and the mass percent of each main alloy element is：C 0.45~0.60%, Si≤0.30%, Mn≤0.30%, Cr 3.00~4.50%, Mo 0.30~0.80%, V 0.30~0.60%, Al 0.50~0.90%, P ＜ 0.015%, S ＜ 0.015%, Fe surpluses.High resistance to tempering is obtained by the balance of Cr, Mo, while can form AlN high abrasion hardening constituents through surface carburization processing after addition Al in the base.The preparation process of steel of the present invention is as follows：Dispensing, smelting, pouring, then electroslag remelting, annealing；Then high-temperature homogenization heat treatment, multiway forging, annealing；Ultrafining heat-treatment and isothermal annealing processing are carried out again；Finally carry out quenching and tempering treatment.Have many advantages, such as high abrasion and excellent resistance to tempering under the conditions of steel of the present invention is at low cost, toughness is suitable with H13 steel.
Description
Technical field
The invention belongs to steel alloy manufacturing process technology fields, are specifically related to a kind of economical extrusion die steel containing aluminothermy
And its preparation, heat treatment and surface treatment method.
Background technology
Hot-extrusion mold is on active service under the mal-conditions such as high temperature, high pressure, abrasion and heat fatigue.Hot extrusion is plasticity
Metal stock forms the required proximate matter of shape or the process of tubing by extrusion die profile under the effect of the pressure.China's mesh
Preceding Extrusion Die Steel is using the 3Cr2W8V and H13 (4Cr5MoSiV1) steel in standard GB/T/T 1299-2000.
Traditional Extrusion Die Steel is 3Cr2W8V, starts industrially to use the 1920s, be widely used in black
Color and non-ferrous metal hot extruding die are a kind of hot die steels of high heat-intensity, and have good forging and machining property
Can, temperature in use can reach 650 DEG C.But W steel series dies thermal conductivity and thermal fatigue resistance are poor, modeling, toughness are low, are easy hair
Raw early fracture.In the early 1980s, the general chromium series hot die steel H13 (4Cr5MoSiV1) of China's Introduced From Abroad,
Compared with high heat-intensity hot-work die steel 3Cr2W8V, H13 has high toughness and thermal fatigue resistance, therefore can replace because tough
Property or thermal fatigue it is insufficient and cause the 3Cr2W8V steel of failure to manufacture hot extruding die, but this replacement is generally limited to make
Under conditions of being no more than 600 DEG C with temperature, other than temperature in use is subject to certain restrictions, there is also have larger ruler for H13 steel
Very little effect (dimensional effect, which refers to many materials, can lose the utilizable property of original when change in size is to a certain limit),
After section is more than 120mm × 120mm, center portion transverse toughness is remarkably decreased, and center portion impact flexibility also only has longitudinal surface
30~40%.
Hot extrusion is primarily upon wearability, anti-temper softening ability and cold-and-heat resistent with hot die steel in use
Fatigue behaviour.For H13 steel as Extrusion Die Steel, chemical analysis contains higher molybdenum, chromium and v element and a certain amount of carbon
Element belongs to hypereutectoid steel, therefore the segregation of its material ESR ingot is serious, and there are the carbonizations of some liquations in the tissue after becoming a useful person
Object causes the toughness of material insufficient.In addition, forming high rigidity nitration case on the cavity channel of hot extruding die can significantly improve
The surface quality of die life and extrudate, thus Extrusion Die Steel should have good nitriding ability, and tradition H13 steel into
For the hardness of row surface carburization processing in 900~1000HV, wearability is inadequate.
Invention content
Defect in view of the prior art, the object of the present invention is to provide a kind of extrusion die steel containing aluminothermy and its producers
Method.
The technical solution used in the present invention is：One kind extrusion die steel containing aluminothermy and its production method, the steel is by weight
Meter includes that the mass percent of element is：C 0.45~0.60%, Si≤0.30%, Mn≤0.30%, Cr 3.00~
4.50%, Mo 0.30~0.80%, V 0.30~0.60%, Al 0.50~0.90%, P ＜ 0.015%, S ＜ 0.015%,
Surplus is Fe；Above-mentioned Si, Mn, V, P, S is all higher than zero, and the production stage of above-mentioned steel includes as follows：
Step 1 is smelted：Dispensing is carried out by above-mentioned mass percent, then uses induction melting or arc melting, is melted
Steel ingot is poured into after refining, waits for using in next step；
Step 2, electroslag remelting：Steel ingot after step 1 pouring is positioned over as consutrode in electroslag remelting device,
Carry out electroslag remelting, slugging 55~65V of voltage, 3500~5500A of electric current；Electric system is：55~60V of voltage, electric current 11500~
12500A, bind 58~62V of voltage；Further float by wash heat and in molten bath removal of inclusions；To eliminate or mitigate
Various both macro and micro defects, improve the ingredient and structural homogenity of steel ingot；
Step 3, the furnace cooling after 750 DEG C~850 DEG C heat preservations 8~10 hours after electroslag remelting；
Step 4, high temperature homogenization：Homogenization temperature is 1200~1260 DEG C, and the homogeneity time is 8~12h；
Step 5, forging：To pass through high temperature homogenization heat treatment steel ingot be cooled in 1080~1180 DEG C of temperature ranges into
Row multiway forging is processed, forging ratio >=6, final forging temperature >=900 DEG C；
Step 6, forging rear annealing：8~10 hours are kept the temperature in 840 DEG C~890 DEG C, furnace cooling；
Step 7, fine：Fine temperature is 1090~1130 DEG C, and the fine time is 7~12h；Then oil cooling or
Water cooling is to 250 DEG C or less；Reheating sends heat-treatment furnace back to, waits for the next step；
Step 8, isothermal annealing：First stage isothermal annealing temperature is 820~840 DEG C, and annealing time is 6~8h；Second
Stage isothermal annealing temperature is 710~740 DEG C, and annealing time is 8~12h；
Step 9, heat treatment：1030~1100 DEG C of quenchings, using oil cooling or gas cooling；Then carry out 560~630 DEG C
Temper, three times, tempering every time keeps the temperature 2~4 hours for tempering；
Step 10, surface treatment：530~570 DEG C of 8~12h of nitriding, nitriding atmosphere are ammonia, 580~620mL/ of flow
Min, 630~670Pa of air pressure in stove.
Compared with prior art, it is an advantage of the invention that：Through alloy optimization design and recommend heat treatment process, overcomes
The widely used H13 steel of hot extruding die resistance to tempering and inadequate disadvantage of wearability under the conditions of same toughness at present.With it is common
H13 steel compare, improve C, reduce Si, Cr, Mo content, alloy total content ratio H13 few 2.5~3.5% reduces hot extrusion
The cost of alloy of compression mould steel；Steel grade of the present invention is set to obtain high resistance to tempering by the balance of Cr, Mo；Al is added in matrix simultaneously
Element can form AlN hardening constituents after surface carburization, and hardness is up to 1100HV or more, and the surface than being formed after H13 steel nitridings is hard
High 100~150HV, and about 80~120 μm of increase after the alloying layer thickness ratio H13 steel nitridings after steel nitriding of the present invention are spent, greatly
Improve hot extruding die surface abrasion resistance greatly.
Description of the drawings
Fig. 1 is that the embodiment of the present invention 1 and H13 steel are quenched and be tempered the comparison of state impact flexibility.
Fig. 2 is that the embodiment of the present invention 1 is compared with H13 steel thermal stability.
Fig. 3 is that the embodiment of the present invention 1 is compared with H13 steel nitriding layer microhardness gradients.
Fig. 4 is the embodiment of the present invention 1 and H13 steel nitriding layer comparison diagrams.
Fig. 5 is that the embodiment of the present invention 2 and H13 steel are quenched and be tempered the comparison of state impact flexibility.
Fig. 6 is that the embodiment of the present invention 2 is compared with H13 steel thermal stability.
Fig. 7 is that the embodiment of the present invention 2 is compared with H13 steel nitriding layer microhardness gradients.
Fig. 8 is the embodiment of the present invention 2 and H13 steel nitriding layer comparison diagrams.
Fig. 9 is that the embodiment of the present invention 3 and H13 steel are quenched and be tempered the comparison of state impact flexibility.
Figure 10 is that the embodiment of the present invention 3 is compared with H13 steel thermal stability.
Figure 11 is that the embodiment of the present invention 3 is compared with H13 steel nitriding layer microhardness gradients.
Figure 12 is the embodiment of the present invention 3 and H13 steel nitriding layer comparison diagrams.
Specific implementation mode
Now specific embodiments of the present invention are described below.
Embodiment 1
C:0.56%, Si:0.20%, Mn:0.24%, Cr:3.00%, Mo:0.42%, V:0.36%, Al:0.70%,
P:0.010%, S:0.012%, Fe surplus.
In the present embodiment, steps are as follows for preparation, heat treatment and the process of surface treatment of the economical extrusion die steel containing aluminothermy：
1. electric furnace smelting：Melting is carried out in electric arc furnaces by above-mentioned alloying element proportioning, smelting temperature is more than 1500 DEG C,
It is cast into Ф 400mm electrode bars and air-cooled；
2. electroslag remelting：Steel ingot after pouring is positioned over as consutrode in electroslag remelting device, electroslag weight is carried out
Molten, slugging 55~65V of voltage, 3500~5500A of electric current, electric system are：55~60V of voltage, 11500~12500A of electric current, envelope
58~62V of voltage is pushed up, current time 40min, electroslag remelting is at 500Kg ESR ingots；
3. furnace cooling after keeping the temperature 10 hours in 800 DEG C after electroslag remelting；
4. high-temperature homogenization：By the Heating Steel Ingots after electroslag remelting to 1250 DEG C of progress high temperature homogenization processing, heat preservation 12
Hour, uniform formation mitigates component segregation；
5. forging：High temperature homogenization heat treatment steel ingot will be passed through and be cooled to 1150 DEG C of progress multiway forging processing, forging ratio
>=6,900 DEG C of final forging temperature；
6. forging rear annealing：860 DEG C keep the temperature 10 hours, furnace cooling；
7. fine：Fine temperature is 1120 DEG C, and the fine time is 12h；Then it is cooled to 250 DEG C or less soon；Reheating
Send heat-treatment furnace back to；
8. isothermal annealing：First stage isothermal annealing temperature is 840 DEG C, annealing time 8h；Second stage isothermal annealing
Temperature is 720 DEG C, annealing time 12h；
9. heat treatment：1030 DEG C of quenchings, using oil cooling；600 DEG C of tempers are then carried out, tempering three times, is tempered every time
Heat preservation 2 hours；
10. surface carburization is handled：550 DEG C of nitriding 10h, nitriding atmosphere are ammonia, flow 600mL/min, air pressure in stove
650Pa。
For hot die steel of the present invention after above-mentioned smelting and hot-working and heat treatment, final finished specification is Ф 260mm
Round steel, sampling are tested for the property, and are compared with the H13 steel under equal conditions：
1. tempering state hardness of quenching
Quenching hardness：55HRC；Tempering hardness：45HRC.
2. tempering state impact flexibility of quenching
It is 10mm × 10mm × 55mm that lateral impact sample, specimen size are taken on blank, opens V2 types notch and (uses North America
Die casting association NADCA#207 standards).Room temperature impact work value：Steel grade 18J of the present invention, is more than the 14J of H13 steel, and test result is for example attached
Shown in Fig. 1, reach the super Impact Toughness of Steel requirement of NADCA#207 standards.
3. thermal stability
Steel of the present invention under the conditions of 620 DEG C with H13 steel carry out stability contrast experiment, H13 steel through quenching temper it
After make its hardness number as steel of the present invention, be 45HRC, test result is as shown in Fig. 2.With the extension of soaking time,
Steel of the present invention and H13 steel difference of hardness are increasing, fast, the heat preservation 20h at 620 DEG C of H13 steel hardness suppression ratios steel of the present invention
From the point of view of thermal stability curvilinear motion situation, the anti-temper softening ability of steel of the present invention is better than H13 steel.
4. nitriding layer microhardness gradient
To carrying out vickers hardness test after the specimen cross section grinding and polishing after nitriding from surface layer to matrix, as a result as shown in Fig. 3.
The surface carburization layer hardness about 1200HV of steel of the present invention, and H13 steel is 1000~1050HV, steel nitriding layer case hardness of the present invention
About 150HV higher than H13.
5. nitriding layer tissue
To the specimen cross section after nitriding according to metallographic preparation method, observed after grinding and polishing corrosion, as shown in Fig. 4.And this
100 μm of the increase of the nitrided case depth ratio H13 of invention steel.
Embodiment 2
It is as follows using the chemical composition of the economical extrusion die steel containing aluminothermy in this example：
C:0.45%, Si:0.21%, Mn:0.23%, Cr:3.00%, Mo:0.30%, V:0.30%, Al:0.50%,
P:0.015%, S:0.010%, Fe surplus.
In the present embodiment, steps are as follows for preparation, heat treatment and the process of surface treatment of the economical extrusion die steel containing aluminothermy：
1. electric furnace smelting：Melting is carried out in electric arc furnaces by above-mentioned alloying element proportioning, smelting temperature is more than 1500 DEG C,
It is cast into Ф 400mm electrode bars and air-cooled；
2. electroslag remelting：Steel ingot after pouring is positioned over as consutrode in electroslag remelting device, electroslag weight is carried out
Molten, slugging 55~65V of voltage, 3500~5500A of electric current, electric system are：55~60V of voltage, 11500~12500A of electric current, envelope
58~62V of voltage is pushed up, current time 36min, electroslag remelting is at 500Kg ESR ingots；
3. furnace cooling after keeping the temperature 8 hours in 800 DEG C after electroslag remelting；
4. high-temperature homogenization：By the Heating Steel Ingots after electroslag remelting to 1250 DEG C of progress high temperature homogenization processing, heat preservation 10
Hour, uniform formation mitigates component segregation；
5. forging：High temperature homogenization heat treatment steel ingot will be passed through and be cooled to 1100 DEG C of progress multiway forging processing, forging ratio
>=6,900 DEG C of final forging temperature；
6. forging rear annealing：850 DEG C keep the temperature 10 hours, furnace cooling；
7. fine：Fine temperature is 1080 DEG C, and the fine time is 8h；Then it is cooled to 250 DEG C or less soon；It is heat-fed again
Backheat treatment furnace；
8. isothermal annealing：First stage isothermal annealing temperature is 840 DEG C, annealing time 8h；Second stage isothermal annealing
Temperature is 720 DEG C, annealing time 10h；
9. heat treatment：1030 DEG C of quenchings, using oil cooling；600 DEG C of tempers are then carried out, tempering three times, is tempered every time
Heat preservation 2 hours；
10. surface carburization is handled：550 DEG C of nitriding 10h, nitriding atmosphere are ammonia, flow 600mL/min, air pressure in stove
650Pa。
For hot die steel of the present invention after above-mentioned smelting and hot-working and heat treatment, final finished specification is Ф 260mm
Round steel, sampling are tested for the property, and are compared with the H13 steel under equal conditions：
1. tempering state hardness of quenching
Quenching hardness：53HRC；Tempering hardness：42HRC.
2. tempering state impact flexibility of quenching
It is 10mm × 10mm × 55mm that lateral impact sample, specimen size are taken on blank, opens V2 types notch and (uses North America
Die casting association NADCA#207 standards).Room temperature impact work value：Steel grade 22J of the present invention, is more than the 16J of H13 steel, and test result is for example attached
Shown in Fig. 5, reach the super Impact Toughness of Steel requirement of NADCA#207 standards.
3. thermal stability
Steel of the present invention under the conditions of 620 DEG C with H13 steel carry out stability contrast experiment, H13 steel through quenching temper it
After make its hardness number as steel of the present invention, be 42HRC, test result is as shown in Fig. 6.With the extension of soaking time,
Steel hardness suppression ratio H13 steel of the present invention it is slow, at 620 DEG C keep the temperature 20h thermal stability curvilinear motion situation from the point of view of, the present invention
The anti-temper softening ability of steel is better than H13 steel.
4. nitriding layer microhardness gradient
To carrying out vickers hardness test after the specimen cross section grinding and polishing after nitriding from surface layer to matrix, as a result as shown in Fig. 7.
The surface carburization layer hardness of steel of the present invention is more than 1100HV, and H13 steel is 1000~1050HV, and steel nitriding layer surface of the present invention is hard
About 100HV of the degree higher than H13.
5. nitriding layer tissue
To the specimen cross section after nitriding according to metallographic preparation method, observed after grinding and polishing corrosion, as shown in Fig. 8.The present invention
About 80 μm of the increase of the nitrided case depth ratio H13 of steel.
Embodiment 3
It is as follows using the chemical composition of the economical extrusion die steel containing aluminothermy in this example：
C:0.60%, Si:0.18%, Mn:0.20%, Cr:4.50%, Mo:0.80%, V:0.60%, Al:0.90%,
P:0.015%, S:0.010%, Fe surplus.
In the present embodiment, steps are as follows for preparation, heat treatment and the process of surface treatment of the economical extrusion die steel containing aluminothermy：
1. electric furnace smelting：Melting is carried out in electric arc furnaces by above-mentioned alloying element proportioning, smelting temperature is more than 1500 DEG C,
It is cast into Ф 400mm electrode bars and air-cooled；
2. electroslag remelting：Steel ingot after pouring is positioned over as consutrode in electroslag remelting device, electroslag weight is carried out
Molten, slugging 55~65V of voltage, 3500~5500A of electric current, electric system are：55~60V of voltage, 11500~12500A of electric current, envelope
58~62V of voltage is pushed up, current time 48min, electroslag remelting is at 500Kg ESR ingots；
3. furnace cooling after keeping the temperature 10 hours in 850 DEG C after electroslag remelting；
4. high-temperature homogenization：By the Heating Steel Ingots after electroslag remelting to 1250 DEG C of progress high temperature homogenization processing, heat preservation 12
Hour, uniform formation mitigates component segregation；
5. forging：Progress multiway forging in 1180 DEG C of temperature ranges will be cooled to by high temperature homogenization heat treatment steel ingot to add
Work, forging ratio >=6,920 DEG C of final forging temperature；
6. forging rear annealing：880 DEG C keep the temperature 10 hours, furnace cooling；
7. fine：Fine temperature is 1130 DEG C, and the fine time is 12h；Then it is cooled to 250 DEG C or less soon；Reheating
Send heat-treatment furnace back to；
8. isothermal annealing：First stage isothermal annealing temperature is 840 DEG C, annealing time 8h；Second stage isothermal annealing
Temperature is 740 DEG C, annealing time 12h；
9. heat treatment：1030 DEG C of quenchings, using oil cooling；600 DEG C of tempers are then carried out, tempering three times, is tempered every time
Heat preservation 2 hours；
10. surface carburization is handled：550 DEG C of nitriding 10h, nitriding atmosphere are ammonia, flow 600mL/min, air pressure in stove
650Pa。
For hot die steel of the present invention after above-mentioned smelting and hot-working and heat treatment, final finished specification is Ф 260mm
Round steel, sampling are tested for the property, and are compared with the H13 steel under equal conditions：
1. tempering state hardness of quenching
Quenching hardness：57HRC；Tempering hardness：46HRC.
2. tempering state impact flexibility of quenching
It is 10mm × 10mm × 55mm that lateral impact sample, specimen size are taken on blank, opens V2 types notch and (uses North America
Die casting association NADCA#207 standards).Room temperature impact work value：Steel grade 17J of the present invention, is more than the 13J of H13 steel, and test result is for example attached
Shown in Fig. 9, reach the super Impact Toughness of Steel requirement of NADCA#207 standards.
3. thermal stability
Steel of the present invention under the conditions of 620 DEG C with H13 steel carry out stability contrast experiment, H13 steel through quenching temper it
After make its hardness number as steel of the present invention, be 46HRC, test result is as shown in Fig. 10.With the extension of soaking time,
H13 steel hardness suppression ratios steel of the present invention it is fast, at 620 DEG C keep the temperature 20h thermal stability curvilinear motion situation from the point of view of, the present invention
The anti-temper softening ability of steel is better than H13 steel.
4. nitriding layer microhardness gradient
To carrying out vickers hardness test after the specimen cross section grinding and polishing after nitriding from surface layer to matrix, as a result such as 11 institute of attached drawing
Show.The surface carburization layer hardness of steel of the present invention is 1230HV, and H13 steel is 1000~1050HV, and steel nitrided surface of the present invention is hard
About 180HV of the degree higher than H13.
5. nitriding layer tissue
To the specimen cross section after nitriding according to metallographic preparation method, observed after grinding and polishing corrosion, as shown in Fig. 12.And this
120 μm of the increase of the nitrided case depth ratio H13 of invention steel.
The present invention improves C content on the basis of H13 steel, reduces Si, Cr, Mo content, and alloy total content ratio H13 is few about
2.5~3.5%, high resistance to tempering is obtained by the balance of Cr, Mo, while being handled in the base through surface carburization after addition Al can
AlN high abrasion hardening constituents are formed, anti-temper softening ability is solved after H13 steel surface Nitrizing Treatments and wearability is inadequate lacks
It falls into.Meanwhile the reduction of alloy content has been greatly reduced production cost, it is made to have high cost performance.Therefore, the present invention is full
The present situation that the current hot extruding die special-purpose steel kind in the China Zu Liao lacks makes China have independent development high-performance, long-life heat
The ability of extrusion die steel.This patent makes full use of alloying element steady with high tempering is compared using economic alloyage process
Qualitative and wearability effect, addition Al elements promote nitriding ability, and exploitation has the economy of high resistance to tempering and nitriding ability
Type extrusion die steel containing aluminothermy, resistance to tempering are three times of H13 steel.
Claims (1)
1. a kind of extrusion die steel containing aluminothermy and its production method, which is characterized in that the steel includes the quality of element by weight
Percentage is：C 0.45~0.60%, Si≤0.30%, Mn≤0.30%, Cr 3.00~4.50%, Mo 0.30~
0.80%, V 0.30~0.60%, Al 0.50~0.90%, P ＜ 0.015%, S ＜ 0.015%, surplus Fe；Above-mentioned steel
Production stage includes as follows：
Step 1 is smelted：Dispensing is carried out by above-mentioned mass percent, induction melting or arc melting are then used, after melting
Steel ingot is poured into, waits for using in next step；
Step 2, electroslag remelting：Steel ingot after step 1 pouring is positioned over as consutrode in electroslag remelting device, is carried out
Electroslag remelting, slugging 55~65V of voltage, 3500~5500A of electric current；Electric system is：55~60V of voltage, electric current 11500~
12500A, bind 58~62V of voltage；Further float by wash heat and in molten bath removal of inclusions；
Step 3, the furnace cooling after 750 DEG C~850 DEG C heat preservations 8~10 hours after electroslag remelting；
Step 4, high temperature homogenization：Homogenization temperature is 1200~1260 DEG C, and the homogeneity time is 8~12h；
Step 5, forging：It is more it will to be cooled to progress in 1080~1180 DEG C of temperature ranges by high temperature homogenization heat treatment steel ingot
It is processed to forging, forging ratio >=6, final forging temperature >=900 DEG C；
Step 6, forging rear annealing：8~10 hours are kept the temperature in 840 DEG C~890 DEG C, furnace cooling；
Step 7, fine：Fine temperature is 1090~1130 DEG C, and the fine time is 7~12h；Then oil cooling or water cooling
To 250 DEG C or less；Reheating sends heat-treatment furnace back to, waits for the next step；
Step 8, isothermal annealing：First stage isothermal annealing temperature is 820~840 DEG C, and annealing time is 6~8h；Second stage
Isothermal annealing temperature is 710~740 DEG C, and annealing time is 8~12h；
Step 9, heat treatment：1030~1100 DEG C of quenchings, using oil cooling or gas cooling；Then carry out 560~630 DEG C of tempering
Processing, three times, tempering every time keeps the temperature 2~4 hours for tempering；
Step 10, surface treatment：530~570 DEG C of 8~12h of nitriding, nitriding atmosphere are ammonia, 580~620mL/min of flow, stove
Interior 630~670Pa of air pressure.
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Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109797304A (en) * | 2019-01-28 | 2019-05-24 | 上海钰灏新材料科技有限公司 | Preparation method and its hot-work steel material through gas nitriding processing |
| CN110055464A (en) * | 2019-04-29 | 2019-07-26 | 上海工程技术大学 | Tough hot stamping die steel of a kind of fine grain height and preparation method thereof |
| CN110317934A (en) * | 2019-06-20 | 2019-10-11 | 河钢股份有限公司 | Improve the heat treatment process of H13 steel annealed structure uniformity |
| CN110484701A (en) * | 2019-09-02 | 2019-11-22 | 钢铁研究总院 | A kind of heat treatment process of the low deformation rate of large die-casting mould steel high tenacity |
| CN113151641A (en) * | 2021-04-21 | 2021-07-23 | 中山市江润金属压铸有限公司 | Mold activation method capable of prolonging service life of mold |
| CN114318136A (en) * | 2021-06-02 | 2022-04-12 | 中航上大高温合金材料股份有限公司 | Manufacturing method of economical hot-work die steel |
| CN117385287A (en) * | 2023-12-11 | 2024-01-12 | 宁波众远新材料科技有限公司 | Alloy steel and preparation method thereof |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103334054A (en) * | 2013-06-18 | 2013-10-02 | 上海大学 | Economical aluminium-containing hot extrusion mold steel and preparation, heat treatment and surface treatment method thereof |
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2017
- 2017-03-20 CN CN201710164963.9A patent/CN108531821A/en not_active Withdrawn
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103334054A (en) * | 2013-06-18 | 2013-10-02 | 上海大学 | Economical aluminium-containing hot extrusion mold steel and preparation, heat treatment and surface treatment method thereof |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN109797304A (en) * | 2019-01-28 | 2019-05-24 | 上海钰灏新材料科技有限公司 | Preparation method and its hot-work steel material through gas nitriding processing |
| CN110055464A (en) * | 2019-04-29 | 2019-07-26 | 上海工程技术大学 | Tough hot stamping die steel of a kind of fine grain height and preparation method thereof |
| CN110055464B (en) * | 2019-04-29 | 2020-07-17 | 上海工程技术大学 | Fine-grain high-toughness hot stamping die steel and preparation method thereof |
| CN110317934A (en) * | 2019-06-20 | 2019-10-11 | 河钢股份有限公司 | Improve the heat treatment process of H13 steel annealed structure uniformity |
| CN110484701A (en) * | 2019-09-02 | 2019-11-22 | 钢铁研究总院 | A kind of heat treatment process of the low deformation rate of large die-casting mould steel high tenacity |
| CN110484701B (en) * | 2019-09-02 | 2020-08-14 | 钢铁研究总院 | Heat treatment process for high-toughness low-deformation-rate large-scale die-casting die steel |
| CN113151641A (en) * | 2021-04-21 | 2021-07-23 | 中山市江润金属压铸有限公司 | Mold activation method capable of prolonging service life of mold |
| CN114318136A (en) * | 2021-06-02 | 2022-04-12 | 中航上大高温合金材料股份有限公司 | Manufacturing method of economical hot-work die steel |
| CN117385287A (en) * | 2023-12-11 | 2024-01-12 | 宁波众远新材料科技有限公司 | Alloy steel and preparation method thereof |
| CN117385287B (en) * | 2023-12-11 | 2024-03-08 | 宁波众远新材料科技有限公司 | Alloy steel and preparation method thereof |
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