CN107653416A - One kind has high tenacity, high iso advanced hot die steel - Google Patents

One kind has high tenacity, high iso advanced hot die steel Download PDF

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Publication number
CN107653416A
CN107653416A CN201710716046.7A CN201710716046A CN107653416A CN 107653416 A CN107653416 A CN 107653416A CN 201710716046 A CN201710716046 A CN 201710716046A CN 107653416 A CN107653416 A CN 107653416A
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die steel
hot die
hot
tropism
carbide
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CN107653416B (en
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冯明明
刘道献
赵伟东
曹立军
姚宏康
张健
张长春
张海英
王建华
崔瑞婷
蒋大鹏
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Tangshan Zhiwei Yulong Roll Technology Co ltd
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TANGSHAN ZWELL TECHNOLOGY Co Ltd
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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
    • 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
    • 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
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • 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
    • 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
    • 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum

Abstract

The present invention relates to high tenacity, high iso hot die steel ZW868, it is 0.35 0.40% to form as C, Si≤0.25%, Mn is 0.30 0.50%, Cr is 5.00 5.30%, and Mo is 2.20 2.40%, and V is 0.50 0.65%, P≤0.010%, S≤0.001%, Ni≤0.20%, Cu≤0.10%, Nb is 0.005 0.020%, and surplus is Fe and inevitable impurity.The mould steel spheroidizing state microscopic structure is uniform, there is preferable spherodized structure and the crystal grain distribution of fine uniform；Impact fracture pattern has more quasi- understanding face and dimple band to make it have high tenacity, high tropism.Available for hot-extrusion mold is manufactured, plug, die hammer hammer mould, forging press mould, use for finish forge machine mould especially can be as with the high-end compression mod of aluminium, copper and its alloy.

Description

One kind has high tenacity, high iso advanced hot die steel
Technical field
The invention belongs to technical field of alloy steel, and in particular to one kind has high tenacity, high iso advanced Forming Die Has steel ZW868, the product is applied to the use of high-end compression mod.
Background technology
Hot die steel is the important component of mould steel, is mainly used for making red-hot solid-state under certain load Metal produces plastic deformation, or the solid metallic or high-temp liquid metal that would be heated to more than recrystallization temperature as die casting It is compressing.Compared with the purposes of other moulds, its working environment is more severe, and its alloying element content is higher.With Modern manufacturing industry proposes more to large-scale, complicated, accurate, high efficiency, the development in high life direction to the performance of hot die steel High requirement.Hot die steel ZW868 proposed by the present invention, based on H13 steel, using reducing, Si, V content and raising Mo are first Micro Nb being added to steel grade while cellulose content and carrying out alloying element design, the preferable structure property of the product and mechanical property are more Requirement of the modern production to high terminal mould is adapted to well.
The content of the invention
The present invention proposes a kind of with high tenacity, high iso advanced hot die steel ZW868.Wherein ZW868 is should The trade mark title of hot die steel.The product annealed state microstructure is uniform, there is preferable spherodized structure and fine uniform Crystal grain distribution, tempered structure of quenching is uniform, and the tiny precipitated phase of Mo, Cr carbide plays dispersion-strengtherning work in use With improving the performance of material, make material that there is high tenacity, high tropism.The product can be widely used for manufacturing hot-extrusion mold, The hammer mould of plug, die hammer, forging press mould, use for finish forge machine mould especially can be as with the high-end of aluminium, copper and its alloy Compression mod.
Realized especially by following technological means：
A kind of high tenacity, high tropism hot die steel, content is calculated as the hot die steel by mass percentage：C is 0.35-0.40%, Si≤0.25%, Mn 0.30-0.50%, Cr 5.00-5.30%, Mo 2.20-2.40%, V are 0.50-0.65%, P≤0.010%, S≤0.001%, Ni≤0.20%, Cu≤0.10%, Nb 0.005-0.020%, it is remaining Measure as Fe and inevitable impurity.
The hot die steel spheroidizing state microstructure is uniform, and tiny spherical proeutectoid carbide is uniformly distributed in On ferrite matrix, the secondary carbon in (3.45~4.72) × 104 is dispersed with every square millimeter of ferrite base bulk area in section Compound, the size range of the proeutectoid carbide is in 400~1000nm.
The hot die steel is incubated 30min, oil quenching to room temperature, 605 DEG C are tempered 2 times through 1025 ± 10 DEG C of austenitizings Afterwards, in the microstructure in centre：The carbide that main body is Mo and Cr disperse educt on matrix, it is shaped as irregular spherical Or elongated rod shape, equivalent diameter or length range are in 80~300nm.
Hot die steel fracture apperance main body after impact is defined cleavage surface and dimple band.
The types of bodies of the proeutectoid carbide of the spheroidizing is M23C6, M7C3 and M6C type, in M23C6 and M7C3 Bulk alloy element be Cr, the bulk alloy element in M6C is Mo and Cr.
Described 1025 ± 10 DEG C of austenitizings in hot die steel core position, 30min is incubated, oil quenching, is at least tempered 2 It is secondary, carry out non-notch impact, it is ensured that single non-notch side knock work(>=380J, average intact during 45 ± 1HRC of final hardness Mouth side knock performance >=400J；The ratio between horizontal, longitudinal non-notch ballistic work (etc. tropism) >=0.96.
The method of the above-mentioned microstructure of the present invention as follows obtains：
(1) electric furnace smelting, the dispensing of the pig iron and alloy material is carried out according to the constituent content of hot die steel, is melted in electric furnace Change and smelt, aoxidize and skim when temperature is 1630~1650 DEG C, Antaciron, lime, fluorite are added after skimming, tapping temperature is 1650~1660 DEG C, in tapping process plus aluminium carries out deoxidation.
(2) LF stoves refine, and connect argon gas after entering LF stoves, then feeding temperature-raising, add lime and fluorite adjustment clinker flowing Property, using SiC powder and aluminum shot diffusive deoxidation, the heating and thermal insulation time is 10~20min, slag in vain after sampling analysis, white slag keep when Between be 30~50min, trimming is carried out according to analysis result after sampling analysis, LF stoves tapping temperature is 1680~1690 ℃。
(3) VD is refined, final vacuum ＜ 67Pa, is kept 18~35min of the final vacuum, is sampled and divide after vacuum breaker Analysis, the qualified rear soft blow of composition enter argon gas to bull ladle, and the time of soft blow argon gas is 18~39min, and bull ladle temperature is 1550~1568 ℃。
(4) casting electrode base, preheating ingot mould is 80~200 DEG C, is then filled with argon gas to ingot mould, during each wharve applying argon gas Between be 3~5min, then withdraw from tunger tube, cast after ingot mould is covered with lid, casting overall process is using carrying additionally asbestos The argon gas protective casting part of cloth is protected, and argon gas protection flow is 15~26m3/ h, casting time are 4~8min, electrode billet It is stripped after a diameter of 560~610mm, 3~5h.
(5) anneal, 710~760 DEG C of annealing temperature, 1~1.5min/mm of soaking time, be furnace-cooled to 300~350 DEG C.
(6) electroslag remelting, the electrode billet obtained using step (4), removing surface polishing, using calcirm-fluoride and aluminum oxide two First slag system is smelted, and the molten speed value of the starting point of electroslag smelting steady-state process be 7~10kg/min, and the molten speed value of terminal is 5.0~ 8.0kg/min, ESR ingot is obtained, then send forging process after the cold 80~100min of power failure stove.
(7) forge, the ESR ingot that step (6) obtains is heated to 1240~1260 DEG C, 15~25h of insulation is diffused Homogenize, then through upset pulling hammer cogging, be then again heated to 1240~1260 DEG C, 15~25h of insulation is diffused Homogenize, then carry out again tri- directions of X, Y and Z it is upset after pull out again to finished size.
(8) ultra fine, the workpiece that step (7) obtains is inserted in heating furnace and is warming up to 1010~1040 DEG C with stove, After being incubated 5~10h, cooled down using the gap type of cooling of sky-water-sky-water, be specially：Come out of the stove be air-cooled to surface 840~ At 860 DEG C, quickly it is put into 25~30 DEG C of water and is cooled down, after water cooling to 860 DEG C~890 DEG C of central temperature, air cooling 2~ 5min, then reenter after being water-cooled to 700 DEG C~730 DEG C of central temperature, 2~5min of air cooling, enter back into and center portion is cooled in water 540 DEG C~560 DEG C or so of temperature, then workpiece is cooled down into 0.5h~2h in atmosphere so that workpiece surface highest returns warm temperature and is 300~330 DEG C, treat that surface temperature carries out spheroidizing for 250 DEG C of -300 DEG C or so fed to boiler.
(9) spheroidizing, the workpiece that step (8) obtains is inserted in annealing furnace, is heated to 830~860 DEG C, insulation 25~ 45h, spheroidizing is carried out, obtains the product of spheroidizing.
Then the specific processing step of performance detection is carried out：
(10) cut horizontal, longitudinal non-notch impact specimen along the centre in section on blank, specimen size be 7mm × 10mm × 55mm, sample, to 1020~1040 DEG C, are incubated 30min oil quenchings to room temperature with stove heat.
(11) it is tempered, the impact specimen obtained after step (10) is quenched is inserted in tempering furnace, is heated to 600~630 DEG C, soaking time 120min, then it is air-cooled to room temperature.
(12) tempering step of repeat step (11) 2~3 times so that impact specimen hardness is carried out after reaching 44~46HRC Ballistic work performance detection.
Effect of the invention is that：
1, the mold materials spheroidizing state microstructure is uniform, and tiny spherical proeutectoid carbide is uniformly distributed in iron On ferritic matrix, its density is per 1mm2(3.45~4.72) × 10 are dispersed with area4Individual carbide, the chi of proeutectoid carbide For very little scope in 400~1000nm, the type of carbide mainly has M23C6, M7C3, M6C type, contained by different types of carbide Main alloy element it is different, the main alloy element in M23C6 and M7C3 be Cr, the main alloy element in M6C for Mo with Cr；Graded by NADCA#207-2011 standards, rank reaches within AS6.The spherodized structure is advantageous to austenitization Fully dissolving, reduce undissolved carbide quantity and size.Tempered process disperse educt again, reach the mesh for improving impact flexibility 's.
2, the mold materials most of alloying elements in quenching process are dissolved into matrix, from matrix in drawing process The carbide of upper disperse educt, predominantly Mo, Cr.Exactly these tiny precipitated phases play dispersion-strengtherning work in use With improving the performance of material.The single non-notch side knock work(>=380J of the mold materials center portion, average non-notch laterally rush Hit performance >=400J；The ratio between horizontal, longitudinal non-notch ballistic work (etc. tropism) >=0.96.
Brief description of the drawings
Fig. 1 is hot die steel spheroidizing organization chart of the present invention.
Fig. 2 is the microstructure schematic diagram of hot-work die tempered structure of the present invention.
Fig. 3 is a kind of embodiment position impact specimen microfractograph schematic diagram of hot-work die of the present invention.
Fig. 4 is a kind of other position impact specimen microfractograph schematic diagram of embodiment of hot-work die of the present invention.
Embodiment
Embodiment 1
A kind of high tenacity, high tropism ZW868 hot forming dies materials, the composition and its percentage composition of the mold materials are：
Surplus is Fe and inevitable impurity.
Embodiment 2
A kind of high tenacity, high tropism ZW868 hot forming dies materials, the composition and its percentage composition of the mold materials are：
Surplus is Fe and inevitable impurity.
Embodiment 3
A kind of high tenacity, high tropism ZW868 hot forming dies materials, the composition and its percentage composition of the mold materials are：
Surplus is Fe and inevitable impurity.
Sampling carries out microstructure observation on high tenacity of the present invention, high tropism ZW868 die steel materials and performance is surveyed Examination：
Spheroidizing tissue：In cross section, center portion samples, in 500 × times lower progress spheroidizing histological test, tiny ball Shape proeutectoid carbide is uniformly distributed on ferrite matrix, and its density is per 1mm2(3.45~4.72) × 10 are dispersed with area4 Individual carbide, the size range of proeutectoid carbide mainly have M23C6, M7C3, M6C in 400~1000nm, the type of carbide Type, the main alloy element contained by different types of carbide is different, and the main alloy element in M23C6 and M7C3 is Cr, M6C In main alloy element be Mo and Cr；Accompanying drawing 1, to be graded by NADCA#207-2011 standards, rank reaches within AS6, Uniform spherodized structure, finally to quench, tempering heat treatment performs structural preparation；
Grain size：In the position sample of cross section 1/2, sample is through 1020 DEG C of austenitizings, insulation 30min, and grade quench is extremely 710 DEG C of insulation 30min, are then air-cooled to room temperature.Uniform small grains, reach 8.0 grades of 6394 grain sizes of GB/T；
Quench tempered structure：Sample is incubated 30min, oil quenching, 605 DEG C are tempered 2 times through 1025 ± 10 DEG C of austenitizings.Quenching During most of alloying elements be dissolved into matrix, in drawing process from matrix disperse educt, they are irregular ball The carbide of shape or elongated rod shape, equivalent diameter or length range in 80~300nm, predominantly Mo, Cr.As shown in Figure 2.Just It is that these tiny precipitated phases play dispersion-strengthened action in use, improves the performance of material；
Impact flexibility is tested：Lateral impact sample is taken on blank, specimen size is 7mm × 10mm × 55mm, and sample passes through 1025 ± 10 DEG C of austenitizings, 30min is incubated, oil quenching, 605 DEG C are tempered 2 times, it is ensured that during 45 ± 1HRC of final hardness, single nothing Breach side knock work(>=380J, average non-notch side knock performance >=400J；The ratio between horizontal, longitudinal non-notch ballistic work (etc. Tropism) >=0.96.Specific assay is as shown in table 1；
Impact specimen Fracture scan：An impact specimen (impact value 400J) is taken, its fracture is micro- using scanning electron microscopic observation Pattern is seen, as shown in Figure 3, Figure 4.Formation of crack macro morphology is shown in accompanying drawing 3, and the flatness in fracture macro face reduces, and has tear Obvious characteristic；Fracture origin high power pattern such as Fig. 4, the negligible amounts in grain boundary fracture face, size is smaller, and fracture face major part region is in Existing Quasi cleavage pattern, section big rise and fall, there is more tear feature, torn grain is formed for a large amount of shallow dimples, and dimple size is equal Even and fine small, this is all the good feature of impact flexibility.
Mechanics properties testing the results are shown in Table 1：
The ZW868 mechanical property results of table 1

Claims (3)

1. a kind of high tenacity, high tropism hot die steel, it is characterised in that hot die steel content by mass percentage It is calculated as：C is 0.35-0.40%, Si≤0.25%, Mn 0.30-0.50%, Cr 5.00-5.30%, Mo 2.20- 2.40%, V 0.50-0.65%, P≤0.010%, S≤0.001%, Ni≤0.20%, Cu≤0.10%, Nb 0.005- 0.020%, surplus is Fe and inevitable impurity；
The hot die steel spheroidizing state microstructure is uniform, and tiny spherical proeutectoid carbide is uniformly distributed in iron element On body matrix, (3.45~4.72) × 10 are dispersed with every square millimeter of ferrite base bulk area in section4Individual proeutectoid carbide, The size range of the proeutectoid carbide is in 400~1000nm；
The hot die steel is incubated 30min through 1025 ± 10 DEG C of austenitizings, oil quenching to room temperature, after 605 DEG C of tempering 2 times, in In the tempering state microstructure of quenching of center portion position：The carbide that main body is Mo and Cr disperse educt on matrix, is shaped as irregular Spherical or elongated rod shape, equivalent diameter or length range are in 80~300nm；
Hot die steel fracture apperance main body after impact is defined cleavage surface and dimple band.
2. high tenacity according to claim 1, high tropism hot die steel, it is characterised in that the spheroidizing state The types of bodies of proeutectoid carbide is M23C6, M7C3 and M6C type in microstructure, the bulk alloy in M23C6 and M7C3 Element is Cr, and the bulk alloy element in M6C is Mo and Cr.
3. high tenacity according to claims 1 to 2, high tropism hot die steel, it is characterised in that the hot-work die 1025 ± 10 DEG C of steel core position austenitizing, 30min is incubated, oil quenching, is at least tempered 2 times, carries out non-notch impact, it is ensured that During 45 ± 1HRC of final hardness, single non-notch side knock work(>=380J, average non-notch side knock performance >=400J； The ratio between horizontal, longitudinal non-notch ballistic work (etc. tropism) >=0.96.
CN201710716046.7A 2017-08-10 2017-08-10 One kind having high tenacity, high iso advanced hot die steel ZW868 Active CN107653416B (en)

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Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN109957720A (en) * 2019-02-26 2019-07-02 唐山志威科技有限公司 A kind of development machine cutter ring ZW552 steel of high rigidity, high tenacity
CN109957702A (en) * 2019-02-26 2019-07-02 唐山志威科技有限公司 The preparation method of high rigidity, high tenacity development machine cutter ring steel ZW552
CN110835674A (en) * 2019-10-14 2020-02-25 攀钢集团江油长城特殊钢有限公司 Forging method of tungsten-containing high-chromium martensitic stainless steel
CN111593257A (en) * 2019-09-07 2020-08-28 江苏宏晟模具钢材料科技有限公司 High-toughness and high-thermal-stability hot-work die steel and preparation method thereof
CN113699446A (en) * 2021-08-20 2021-11-26 天津钢研海德科技有限公司 Superfine high-toughness die steel and preparation method thereof
CN114875320A (en) * 2022-05-05 2022-08-09 唐山志威科技有限公司 High-toughness and high-isotropy ZW851 hot-work die steel

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