CN107502832B - A kind of double quenching partition process for high speed tup abrasion-resistant stee steel and preparation method thereof - Google Patents
A kind of double quenching partition process for high speed tup abrasion-resistant stee steel and preparation method thereof Download PDFInfo
- Publication number
- CN107502832B CN107502832B CN201710609331.9A CN201710609331A CN107502832B CN 107502832 B CN107502832 B CN 107502832B CN 201710609331 A CN201710609331 A CN 201710609331A CN 107502832 B CN107502832 B CN 107502832B
- Authority
- CN
- China
- Prior art keywords
- abrasion
- high speed
- tup
- partition process
- resistant
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
Classifications
-
- 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
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
- 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
-
- 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/0068—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for particular articles not mentioned below
-
- 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
- C22C38/22—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
- C22C38/26—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
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Articles (AREA)
Abstract
A kind of double quenching partition process for high speed tup abrasion-resistant stees and preparation method thereof, belong to metal material processing technical field.Double quenching partition process for high speed tups in the present invention are designed with abrasion-resistant stee by reasonable alloy system ingredient, again by innovative double quenchings+with division technique, make the tissue more fine uniform of steel, width of sheet obviously becomes smaller, the duplex structure of the proportion-controllable finally obtained, with high rigidity, high intensity, higher toughness, highly anti-fatigue comprehensive mechanical property.The yield strength R of materialp0.2>=1550MPa, tensile strength Rm>=1950MPa, elongation after fracture A >=13%, strength and ductility product >=25GPa%, V-notch ballistic work >=13J, hardness >=55HRC.The membranaceous retained austenite being distributed between martensite lath not only contributes to coordinate the deformation under tissue stress condition, and the effect for hindering microfissure extension is also clearly, improves the anti-fatigue ability of material and the service life of tup.This double quenching partition process for high speed tups are the ideal material of pulverizer hammer steel with abrasion-resistant stee.
Description
Technical field
The invention belongs to metal material processing technical fields, and it is difficult to understand for lath martensite and remnants to be related to a kind of room temperature texture
Duplex structure's abrasion-resistant stee of family name's body, and the hammer of double quenching partition process for high speed with high rigidity, high-wearing feature and excellent toughness
Head abrasion-resistant stee and its manufacturing method.
Background technique
Hammer mill is broadly divided into two kinds of hammerhead crusher and reaction type bar crusher.Due to hammer mill knot
Structure is simple, high production efficiency and easy to maintenance, is widely used to mine, metallurgy, building materials, highway, railway, water conservancy and electric power etc.
Industry.The material for being commonly used in production tup has potassium steel, abrasion resistant cast steel, high-chromium abrasion-proof cast iron.Hammer mill fragment
Tup or bar are main vulnerable parts when material, and since tup working environment is severe, the impact and abrasion of material can all make to hammer into shape
It is short-lived, it is prone to wear failure.Materials microstructure and mechanical property are particularly important, service life of the strong influence to it
And working efficiency, this requires hammer head materials to have good wearability.
Before about 130 years, British R.A.Hadfield has invented common potassium steel.So far, it is wear-resistant
Important status is still occupied in material.Potassium steel has stronger work hardening capacity, as shock loading increases, table
Face thin hardened layer is bigger, and hardness is higher, and abrasive resistance is better, and inside workpiece still keeps its original high tenacity, high-ductility.
Traditional material of tup is still potassium steel at present.Since the wear form of tup is based on impact wear, and hammer crushing
Suffered impact force does not reach the processing hardening claimed range of potassium steel to machine tup during operation, wear-resisting so as to cause its
Property it is lower, and lead to tup surface deformation during processing hardening, crushing effect is deteriorated, it is easy to cause because of subsequent abrasion
Service life shortens.
It, can when the advantage of potassium steel cannot be brought into play when crusher is worked under the working condition fiercely impacted
It is replaced with casting tup using steel alloy.Steel alloy tup is compared with being suitble to operating condition little in broken material granularity and medium stress
Under the conditions of use.General middle and high carbon low alloy steel and high-alloy steel this few class abrasion-resistant cast steel material are used to manufacture tup casting.
The alloying elements such as nickel, chromium can also be suitably added according to concrete condition to improve the harden ability of material.But under normative heat treatment technique
Tup often toughness is poor, easily there is the case where abrasion, fall.
Since the additive amount of alloying element in low-alloy wear-resistant steel is relatively fewer, carbon content is higher, and hardness is larger, to mention
The wear-resisting property of high material need to centainly match its preparation process and the reasonable design of structural state progress with control, acquisition
Martensite and retained austenite two-phase fine grain structure steel, it is ensured that material has high rigidity, high intensity, higher toughness, highly resistance tired
The good comprehensive performance of labor.Chinese patent application CN200910227804.4 describe a kind of casting obtain hardness 50~
The preparation method of the abrasion-resistant stee of 53HRC, the material composition joined the Re more than 0.1wt%, bring the raising of cost when designing,
And it is carbide and ferrite that prolonged lonneal, which easily leads to a small amount of retained austenite tissue breakdown in material, is brought tough
Property deterioration, elongation is 2.4~3.0%, and plasticity and toughness are far below double quenching partition process for high speed tups use in the present invention
Abrasion-resistant stee.Chinese patent application CN201010575998.X describes a kind of cast and obtains the preparation method of low-alloy wear-resistant steel,
The Material cladding adds the microalloy elements such as C, Si, Mn, Cr, B, Ce, is had by obtaining one kind after oil quenchinng+tempering heat treatment
Tempered martensite's steel, not under conditions of open gap, ballistic work is only 25~40J, and tensile strength is only 1100~
1500MPa, mechanical property are poor.Chinese patent application CN201510520418.X describes a kind of hot rolling and obtains inexpensive high-ductility
Property super abrasion-resistant stee preparation method, which adds the microalloy elements such as C, Si, Mn, Ti, B, by adding up reduction ratio
For 65~80% hot rolling, and after rolling rear section cooling, then heated, salt bath cooling, the complicated heat such as medium temperature+lonneal
After treatment process, a kind of surface is obtained based on tempered martensite, high tenacity of the center portion based on bainite and retained austenite
Wear-resisting steel plate, the yield strength R of materialp0.2=980~1235MPa, tensile strength Rm=1400~1562MPa, elongation after fracture
A=14.2~18.1%, hardness is 412~478HV, after the hot rolling deformation by aximal deformation value, elongation after fracture and this hair
Bright middle abrasion-resistant stee differs very little, however its intensity and hardness far below double quenching partition process for high speed tups in the present invention with resistance to
Grind steel.
In conclusion double quenching partition process for high speed tups in the present invention with abrasion-resistant stee by reasonable alloy system at
Set up meter separately, and innovative double quenchings+match division technique make steel have the duplex structure of proportion-controllable, with high rigidity, high-strength
Degree, higher toughness, highly anti-fatigue comprehensive mechanical property, realize the target of high-wearing feature.Heat treatment process technological parameter is adjusted,
It after quenching twice, is obviously refined in the crystal grain of material, martensite lath mean breadth is in 200nm hereinafter, having lath-shaped
The two-phase structure of martensite and retained austenite.As the result is shown when respectively organized in material shared volume fraction certain
When range, especially when retained austenite control in a certain ratio, the toughness of material can be improved, coordinate the change of crystal grain
Shape, and the ballistic work of a part can be absorbed under the conditions of severe impact, make retained austenite that the transition process to martensite occur,
Improve the hardness of matrix.Mutually coordinated cooperation between respectively organizing during military service, lath martensite tissue can be improved material
Intensity, metastable retained austenite undergoes phase transition induced plastic effect, allows the material to bear biggish load and deformation, tool
There are good plasticity and shock resistance, yield strength Rp0.2>=1550MPa, tensile strength Rm >=1950MPa, elongation of having no progeny
Rate A >=13%.Membranaceous retained austenite effect of the more uniform distribution for obstruction microfissure extension in the base simultaneously
Also clearly, the anti-fatigue ability for substantially increasing material improves the service life of tup.Therefore this double quenching partition works
The alloying component content of skill high speed tup abrasion-resistant stee is low, and excellent combination property is greatly improved production efficiency, is pulverizer hammer
The head ideal material of steel.
Summary of the invention
Requirement for pulverizer hammer steel to the strength of materials and plasticity, the present invention provide a kind of double quenching partition techniques
High speed tup abrasion-resistant stee steel and preparation method thereof, material have ultra-fine lath martensite+residual austenite body tissue, lath-shaped
Mutually coordinated cooperation between martensite and residual austenite body tissue has good intensity and toughness, has high-wearing feature.
The technical scheme is that a kind of double quenching partition process for high speed tup abrasion-resistant stees, chemical component weight
Percentage are as follows: C:0.40~0.60%, Si:0.5~1.5%, Mn:1.5~2.5%, Cr:1.5~2.5%, Mo:0.1~
0.5%, Nb:0.01~0.05%, Ti:0.05~0.25%, surplus are Fe and inevitable impurity.Another mesh of the invention
The preparation method for being to provide double quenching partition process for high speed tup abrasion-resistant stees, specifically includes the following steps:
Step 1: weighing raw material according to design ingredient, smelted, cast, obtain ingot casting, forged after ingot casting is heated, forged
It makes than being 6~8,；
Step 2: tup blank is prepared in step 1 and is warming up to 980~1080 DEG C, 1~1.5h is kept the temperature, is air-cooled to 400
~450 DEG C of temperature, then oil are cooled to room temperature；
Step 3: by step 2 treated tup blank is warming up to 850~950 DEG C, keep the temperature 1~1.5h, be air-cooled to 300~
350 DEG C of temperature, then control and be cooled to 80~140 DEG C, keep the temperature 20~30min；
Step 4: by step 3 treated tup is heated to 350~450 DEG C, keep the temperature 50~80min, water cooling to room temperature, into
Row is necessary to be machined to get double quenching partition process for high speed tup abrasion-resistant stee tups are arrived.
Further, the tissue of double quenching partition process for high speed tup abrasion-resistant stees is lath martensite+residual austenite
Body, the volume ratio of each tissue are as follows: lath martensite 78%~85%, retained austenite 15%~22%；Double quenchings are matched
The martensite lath mean breadth of division technique high speed tup abrasion-resistant stee is less than 200nm.
Further, material room temperature texture of the present invention very fine uniform, lath martensite and two kinds of retained austenite tissues
Ratio is controllable, and retained austenite ratio is controlled 15~22%, remaining is lath martensite, is finally quenched in room temperature process
It does not undergo phase transition.
Further, the yield strength R of double quenching partition process for high speed tups its material of abrasion-resistant steep0.2≥
1550MPa, tensile strength Rm>=1950MPa, elongation after fracture A >=13%, strength and ductility product >=25GPa%, V-notch ballistic work
>=13J, hardness >=55HRC.
The effect of essential element in material of the present invention are as follows:
The increase of C content can greatly improve intensity, the hardness of material, but will cause the serious evil of moulding and toughness
Change.C is the essential element of the important element that austenite is formed and stable austenite, and austenite is to bainite transformation process
In the diffusion of C element occurs simultaneously, C element enrichment is so that it can be stabilized at room temperature in retained austenite.
Si can inhibit the precipitation of the carbide such as cementite, reduce the C being dissolved in ferrite, improve C content in austenite,
To guarantee obtain enough stable residual austenites at room temperature, in steel Si content 1.3% hereinafter, with Si content increasing
Add, intensity, toughness, plasticity increase.
The main function of Mn is enhancing stabilization of austenite, extends it and changes incubation period, improves the intensity and harden ability of steel,
Also Ms is promoted to reduce simultaneously, forms the retained austenite of the rich carbon of certain volume.
Cr can increase the intensity of steel, plasticity, toughness.The wearability of material is improved with the increase of chromium content, when chromium is less than
When 3%, the effect improved to the wearability of material is more significant.Chromium can increase the harden ability of steel, when additional amount is larger, especially and
When Ni, Mo arrange in pairs or groups, the excellent steel grade of harden ability can get.
Mo can significantly improve the intensity and toughness of steel, in addition it can improve the harden ability and temper resistance of steel.
The present invention matches forged forming and heat treatment process by reasonable element, is prepared a kind of multiple with fine grain
The high toughness wear resistant steel of phase constitution, it is partition that uniformly by the diffusion of first time heating alloying component, crystal grain refines significantly after quenching
Tiny and uniform matrix is provided.By matching division technique, retained austenite fixing fabric structure 15~22%, guarantee material have compared with
High obdurability, during military service, metastable retained austenite induced transformation effect also can be further improved material toughness and
Wearability, the complex precipitates that Ti, Nb and C, N are formed can also generate precipitation strength effect, along with refined crystalline strengthening effect can
The comprehensive performance of material is improved to varying degrees.
Detailed description of the invention
Fig. 1 is the heat treatment process schematic diagram of abrasion-resistant stee of the invention；
Fig. 2 is the scanning organization chart picture of the abrasion-resistant stee in the embodiment of the present invention 1；
Fig. 3 is the transmission organization chart picture of the abrasion-resistant stee in the embodiment of the present invention 1；
Fig. 4 is the scanning organization chart picture of the abrasion-resistant stee in the embodiment of the present invention 2；
Fig. 5 is the transmission organization chart picture of the abrasion-resistant stee in the embodiment of the present invention 2.
Specific embodiment
Embodiment 1:
It smelted, cast first, in accordance with mentioned component range, then detected the ingredient of slab, be shown in Table 1.
The ingredient (wt.%) of 1 slab of table
Specific heat treatment process parameter is shown in Table 2.
2 heat treatment process parameter of table
3 are shown in Table according to the mechanical property of double quenching partition process for high speed tup abrasion-resistant stees made from Tables 1 and 2.
3 mechanical property of table
The double quenching partition process for high speed tups being prepared according to Tables 1 and 2 measure remaining Austria by XRD with abrasion-resistant stee
Family name's body volume fraction, martensitic phase volume fraction subtract retained austenite volume fraction for 100%, the results are shown in Table 4.
4 different tissues content of table
Each mechanical property reaches very high mechanical performance index as can be seen from Table 3, yield strength 1572MPa,
Tensile strength is 1993MPa, and elongation 15%, hardness 57HRC, V mouthful ballistic work is 15J.Scanned photograph as shown in Fig. 2,
Photo is transmitted as shown in figure 3, tissue is lath martensite+retained austenite, lath martensite and retained austenite difference Zhan are total
The 81% of volume and 19%, retained austenite is mainly distributed between martensite lath with film-form, and dislocation density is higher.
Embodiment 2:
It smelted, cast first, in accordance with mentioned component range, then detected the ingredient of slab, be shown in Table 5.
The ingredient (wt.%) of 5 slab of table
Specific heat treatment process parameter is shown in Table 6.
6 heat treatment process parameter of table
7 are shown in Table according to the mechanical property of double quenching partition process for high speed tup abrasion-resistant stees made from table 5 and table 6.
7 mechanical property of table
The double quenching partition process for high speed tups being prepared according to table 5 and table 6 measure remaining Austria by XRD with abrasion-resistant stee
Family name's body volume fraction, martensitic phase volume fraction subtract retained austenite volume fraction for 100%, the results are shown in Table 8.
8 different tissues content of table
Each mechanical property reaches very high mechanical performance index as can be seen from Table 7, yield strength 1563MPa,
Tensile strength is 1956MPa, and elongation 14%, hardness 55HRC, V mouthful ballistic work is 13.5J.Scanned photograph such as Fig. 4 institute
Show, as shown in figure 5, tissue is lath martensite+retained austenite, lath martensite and retained austenite account for transmission photo respectively
The 79% of total volume and 21%, retained austenite is mainly distributed between martensite lath with film-form, and dislocation density compares example 1
It is more lower.
It should be noted last that the above embodiments are merely illustrative of the technical solutions of the present invention, rather than limit.Although ginseng
It is described the invention in detail according to embodiment, it will be apparent to an ordinarily skilled person in the art that technical side of the invention
Case is modified or replaced equivalently, and without departure from the spirit and scope of technical solution of the present invention, should all be covered in the present invention
Scope of the claims in.
Claims (2)
1. a kind of preparation method of double quenching partition process for high speed tup abrasion-resistant stees, which comprises the following steps:
Step 1: weighing raw material according to design ingredient, smelted, cast, obtain ingot casting, forged after ingot casting is heated, forging ratio
It is 6 ~ 8；
Step 2: tup blank is prepared in step 1 and is warming up to 980 ~ 1080 DEG C, 1 ~ 1.5h is kept the temperature, is air-cooled to 400 ~ 450 DEG C
Temperature, then oil are cooled to room temperature；
Step 3: by step 2 treated tup blank is warming up to 850 ~ 950 DEG C, keep the temperature 1 ~ 1.5h, be air-cooled to 300 ~ 350 DEG C of temperature
Degree, then control and be cooled to 80 ~ 140 DEG C, keep the temperature 20 ~ 30min；
Step 4: by step 3 treated tup is heated to 350 ~ 450 DEG C, keep the temperature 50 ~ 80min, water cooling to room temperature carries out necessary
Machining to get to double quenching partition process for high speed tup abrasion-resistant stee tups；
The chemical component weight percentage of abrasion-resistant stee are as follows: C:0.40 ~ 0.60%, Si:0.5 ~ 1.5%, Mn:1.5 ~ 1.95%, Cr:1.5
~ 2.5%, Mo:0.1 ~ 0.5%, Nb:0.01 ~ 0.05%, Ti:0.05 ~ 0.25%, surplus are Fe and inevitable impurity；
The volume ratio of each tissue of double quenching partition process for high speed tup abrasion-resistant stees are as follows: lath martensite 78% ~ 85%,
Retained austenite 15% ~ 22%；The average martensite lath width of double quenching partition process for high speed tup abrasion-resistant stees is less than
200nm。
2. the preparation method of double quenching partition process for high speed tup abrasion-resistant stees according to claim 1, which is characterized in that
The yield strength R of materialp0.2>=1550MPa, tensile strength Rm>=1950MPa, elongation after fracture A >=13%, strength and ductility product >=
25GPa%, V-notch ballistic work >=13J, hardness >=55HRC.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201710609331.9A CN107502832B (en) | 2017-07-25 | 2017-07-25 | A kind of double quenching partition process for high speed tup abrasion-resistant stee steel and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201710609331.9A CN107502832B (en) | 2017-07-25 | 2017-07-25 | A kind of double quenching partition process for high speed tup abrasion-resistant stee steel and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN107502832A CN107502832A (en) | 2017-12-22 |
| CN107502832B true CN107502832B (en) | 2019-03-15 |
Family
ID=60689421
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201710609331.9A Active CN107502832B (en) | 2017-07-25 | 2017-07-25 | A kind of double quenching partition process for high speed tup abrasion-resistant stee steel and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN107502832B (en) |
Families Citing this family (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112575256B (en) * | 2020-11-26 | 2021-12-31 | 博耀能源科技有限公司 | High-strength and high-toughness large-diameter wind power bolt with shell/horse complex phase structure and preparation method thereof |
| CN114669599A (en) * | 2022-02-28 | 2022-06-28 | 首钢京唐钢铁联合有限责任公司 | Method for prolonging on-machine time of hammerhead of hot-rolling width-fixing press |
| CN115354217B (en) * | 2022-07-04 | 2023-03-03 | 钢铁研究总院有限公司 | Impact-abrasion-resistant complex-phase structure hammer head and preparation method thereof |
| CN115652045B (en) * | 2022-08-26 | 2024-05-24 | 刘澄 | Preparation method of high-wear-resistance impact-resistant Fe-Cr-Mn-Si-Mo-C-N alloy crusher hammer |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1050566A (en) * | 1989-09-28 | 1991-04-10 | 齐靖远 | Medium carbon alloy steel |
| JPH05239591A (en) * | 1992-02-27 | 1993-09-17 | Nkk Corp | Steel excellent in wear resistance |
| CN103627993A (en) * | 2013-11-11 | 2014-03-12 | 马鞍山市恒毅机械制造有限公司 | Alloy steel hammerhead material for small-size crusher and preparation method thereof |
| CN106435404A (en) * | 2015-08-06 | 2017-02-22 | 江苏金源锻造股份有限公司 | Low wind speed wind power unit low-carbon alloy steel wind power main shaft manufacturing method |
-
2017
- 2017-07-25 CN CN201710609331.9A patent/CN107502832B/en active Active
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1050566A (en) * | 1989-09-28 | 1991-04-10 | 齐靖远 | Medium carbon alloy steel |
| JPH05239591A (en) * | 1992-02-27 | 1993-09-17 | Nkk Corp | Steel excellent in wear resistance |
| CN103627993A (en) * | 2013-11-11 | 2014-03-12 | 马鞍山市恒毅机械制造有限公司 | Alloy steel hammerhead material for small-size crusher and preparation method thereof |
| CN106435404A (en) * | 2015-08-06 | 2017-02-22 | 江苏金源锻造股份有限公司 | Low wind speed wind power unit low-carbon alloy steel wind power main shaft manufacturing method |
Also Published As
| Publication number | Publication date |
|---|---|
| CN107502832A (en) | 2017-12-22 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN100540714C (en) | A kind of snappiness, high-strength steel and manufacture method thereof | |
| CN107502832B (en) | A kind of double quenching partition process for high speed tup abrasion-resistant stee steel and preparation method thereof | |
| US8926768B2 (en) | High-strength and high-ductility steel for spring, method for producing same, and spring | |
| CN114107830B (en) | Low-density wear-resistant steel used in wide temperature range and preparation method thereof | |
| CN104264072B (en) | A kind of 600HB grade wear-resisting steel plate and preparation method thereof | |
| CN109913751A (en) | High-strength tenacity Bainite wear-resisting steel and preparation method thereof suitable for large-scale semi-autogenous mill liner plate | |
| CN107974636A (en) | A kind of high rigidity high-hardenability pre-hardening plastic die steel and preparation method thereof | |
| CN106498294A (en) | A kind of high-level low-alloy wear-resistant steel of NM600 and its application | |
| CN108018492A (en) | A kind of Brinell hardness is more than the high-level low alloy wear resistance steel plate and manufacture method of 550HB | |
| KR101201647B1 (en) | HIGH Cr CAST IRON ARTICLE WITH SUPERIOR HEAT CRACK RESISTANCE AND METHOD FOR HEAT TREATING HIGH Cr CAST IRON MATERIAL | |
| CN109825774A (en) | A kind of preparation method of Bei Maao multi-phase wear-resistant erosion steel | |
| CN110438388B (en) | Preparation method of Australian alternate wear-resistant corrosion-resistant steel | |
| CN105543676A (en) | Martensite-ferrite double-phase wear-resisting steel plate and preparing method thereof | |
| CN105483539A (en) | Superhard particle-reinforced austenite wear-resistant steel plate and manufacturing method thereof | |
| CN101353763A (en) | High hardness wear resistant hot-rolled strip steel and manufacturing method thereof | |
| KR100836699B1 (en) | Die steel | |
| CN114717389B (en) | Wear-resistant low-temperature bainite hot work die steel and preparation method thereof | |
| CN110184527A (en) | It is a kind of for making the high intensity levels non-hardened and tempered steel bar and its manufacturing method of engine rocker | |
| CN108165890A (en) | A kind of preparation method of low-cost high-strength nanometer bainite abrasion-proof steel ball | |
| CN111809114B (en) | Plastic die steel with excellent high-temperature strength and preparation method thereof | |
| CN109457184A (en) | A kind of high-wearing feature steel plate and its production method | |
| CN106893942B (en) | A kind of high intensity bainite antiwear steel plate and its production method | |
| CN102373384A (en) | High-strength high-toughness wear-resistant steel plate and manufacturing method thereof | |
| CN103233171B (en) | A kind of NM400 level cracking resistance line high-strength abrasion-proof steel and production method | |
| CN106676390A (en) | Low-carbon martensite cast steel applied to heavy cross section and heat treatment method of low-carbon martensite cast steel |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |