CN103160717A - Hypereutectic Al-Si alloy modification treatment adopting extrusion casting molding method - Google Patents
Hypereutectic Al-Si alloy modification treatment adopting extrusion casting molding method Download PDFInfo
- Publication number
- CN103160717A CN103160717A CN2011104054435A CN201110405443A CN103160717A CN 103160717 A CN103160717 A CN 103160717A CN 2011104054435 A CN2011104054435 A CN 2011104054435A CN 201110405443 A CN201110405443 A CN 201110405443A CN 103160717 A CN103160717 A CN 103160717A
- Authority
- CN
- China
- Prior art keywords
- molten metal
- hypereutectic
- alloy
- mould
- extrusion casting
- 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.)
- Granted
Links
Images
Abstract
The invention relates to a hypereutectic Al-Si alloy modification treatment adopting an extrusion casting molding method, wherein a modification treatment is performed before a metal liquid is poured, then the metal liquid is injected into a mold, an extrusion head of an extruder rapidly declines, the metal liquid is pressurized so as to carry out forced shrinkage filling and solidification on the metal billet, and the metal billet is taken out after pressure maintaining is performed. With the technical scheme, quality and various performance indexes of products of the present invention are accordingly improved compared to quality and various performance indexes of products produced by the existing technology, and the cast has high strength and high toughness.
Description
Technical field
The present invention relates to the squeeze cast form method, specifically refer to a kind of about the rotten Hypereutectic Al-Si Alloy of processing, the method for employing squeeze cast form.
Background technology
Hypereutectic high-seleium aluminium alloy has that good wear resistance is good, solidity to corrosion is good, hot cracking tendency is little, volume stability is high and the characteristics such as low thermal coefficient of expansion, is the piston alloys such as a kind of desirable new automobile, motorcycle.In this material along with occurring a large amount of primary silicons in the increase tissue of silicon content, the primary silicon that particularly presents thick faller gill shape, seriously isolate alloy substrate, and silicon most advanced and sophisticated and property at parts of edges and corners mutually can cause stress concentration, thereby obviously reduced the mechanical property of alloy, especially affected its plasticity.The method of the refinement silicon phase that adopts at present has multiple, as Suspension Foundry method, spray deposition, ultrasonic vibration method, rapid solidification method etc., though these methods have obtained certain effect, require too harshness owing to being subject to industrial scale restriction and processing condition, thereby all be subject to certain restriction on producing.The mechanical property of hypereutectic high-seleium aluminium alloy foundry goods depends on pattern and the distribution of Si in matrix to a great extent, therefore, improve pattern and the distribution of eutectic Si phase and primary Si phase, not only can put forward heavy alloyed mechanical property, but also can further put forward heavy alloyed wear resistance.Rotten processing to Hypereutectic Al-Si Alloy is mainly the crystallization crystal grain of refinement primary Si phase, the crystal grain of original block primary Si phase and thick needle-like eutectic Si phase is become fine-grannular, to improve its over-all properties.The rotten processing of the primary Si phase of Hypereutectic Al-Si Alloy is mainly by external crystallization nuclei is provided in aluminium alloy, make it become the crystallization nuclei of primary Si phase, thereby crystallization nuclei quantity is increased, grow up to suppress it, realize the uniform purpose of crystal structure refinement.Extrution casting technique is characterized in that material use efficiency is high, and the defectives such as foundry goods internal porosity and shrinkage cavity significantly reduce, grain refining and dense structure etc., and not only can make the alloy structure refinement at Under Pressure Solidification, and the eutectic point of A1-Si alloy is moved to right, reduce thick primary Si phase quantity.Therefore, adopt the mode of squeeze cast form, also can be so that the refinement of hypereutectic A1-Si Silicon In Alloys phase, the mechanical property of alloy increases substantially.To appeal two kinds of techniques and combine, thereby the refinement of assurance silicon phase improved alloy mechanical property, and the while production technique is simple, convenient operation.
Summary of the invention
The invention provides a kind of method for preparing high tough Hypereutectic Al-Si Alloy foundry goods, its objective is: improve Hypereutectic Al-Si Alloy casting compactness, mechanical property and productivity.
For achieving the above object, the present invention is by the following technical solutions:
A kind of rotten processing hypereutectic Al-Si alloy extrusion casting forming method, it is characterized in that: described method is carried out according to following steps:
die tip is provided with the diversion trench that is connected with crucible, utilize tipper that molten metal is injected mould by diversion trench, the molten metal composition is by weight percentage: silicon 17.0～19.0%, copper 1.0～2.0%, magnesium 0.3～0.7%, nickel 0.5～1.0%, iron 0.5～1.0%, manganese 0.3～0.7%, chromium 0.5～1.0%, molybdenum 0.3～0.7%, phosphorus 0.07～0.15%, impurity summation≤0.5%, surplus is aluminium, and the extrusion head of extrusion machine is descended rapidly, begin molten metal is pressurizeed, make the feeding and solidifying by force of metal billet, through after pressurize, billet is taken out.
Before described molten metal injects mould, add alterant processings of go bad, be incubated 5-15min, and then pour into a mould.
Described alterant is strontium, and add-on is the 0.02-0.06% of molten metal total mass, can add with the master alloy form, also can be used as powder and is pressed into molten metal and stirs, and can also add together with refining agent.
Described alterant is phosphorus, and add-on is the 0.5-1.5% of molten metal total mass, can add with the master alloy form, also can be used as powder and is pressed into molten metal and stirs, and can also add together with refining agent.
Before described molten metal injected mould, mould need to be heated to 200～300 ℃, and scribbles coating on mould.
When described molten metal injected mould, the teeming temperature of molten metal was 690～780 ℃.
The lowering speed of described extrusion head is 0.1mm/s～12mm/s, and specific pressure is 70MPa～1500Mpa.
The described dwell time is 10s～60s.
By the enforcement of technical scheme of the present invention, method is simple to operate, is convenient to control, and quality product is high, can improve qualification rate and the production efficiency of high silicon Hypereutectic Al-Si Alloy product.
Description of drawings:
Fig. 1 is extrusion casting metal billet mould structure schematic diagram;
Fig. 2 is the not rotten hypereutectic Al of metal mold gravity casting-17.5Si alloy phase structure;
Fig. 3 is the rotten hypereutectic Al of metal mold gravity casting-17.5Si alloy phase structure;
Fig. 4 is the not rotten hypereutectic Al of metal mold extrusion casting-17.5Si alloy phase structure;
Fig. 5 is the rotten hypereutectic Al of metal mold extrusion casting-17.5Si alloy phase structure;
Fig. 6 is process forming process schematic diagram of the present invention.
Description of reference numerals:
1. extrusion head, 2. diversion trench, 3. cover plate, 4. metal base ingot shape chamber, 5. heating container, 6. choker bar, 7. tightening latch, 8. push rod.
Embodiment:
The present invention adopts metal type dies and extrusion casting method to improve forming technique, the equipment that wherein prepares the Hypereutectic Al-Si Alloy product comprises extrusion machine and metal base ingot mould tool and heat treatment heating furnace, wherein extrusion metal billet mould periphery is resistance wire, utilize resistance wire to mold heated and be provided with thermopair and control die temperature, the mould top is that extrusion head can reach the position that needs extruding by fast-descending, mold bottom is choker bar, hinders molten metal and flows out, and be throwing mechanism below mould.Requirement for extrusion machine is accurately to control squeeze, and the speed when guaranteeing extruding.Heat treatment heating furnace when heating temperature must be evenly and temperature control accurate, otherwise may because of even its degradation of being correlated with that causes of billet tissue odds, not reach requirement.
The present invention is described in detail below in conjunction with accompanying drawing.
As shown in Figure 1, die tip is provided with the diversion trench 2 that is connected with crucible, by tipper, molten metal is injected the metal base ingot shape chamber 4 of moulds by diversion trench 2, is provided with choker bar 6 in 4 bottoms, metal base ingot shape chamber.Before injecting, mould need to heat and scribble coating with heating container 5.The molten metal composition is by weight percentage: silicon 17.0～19.0%, copper 1.0～2.0%, magnesium 0.3～0.7%, nickel 0.5～1.0%, iron 0.5～1.0%, manganese 0.3～0.7%, zirconium 0～0.4%, cerium 0～0.28%, lanthanum 0～0.12%, praseodymium 0～0.02%, niobium 0～0.08%, chromium 0.5～1.0%, molybdenum 0.3～0.7%, phosphorus 0.07～0.15%, impurity summation≤0.5%, surplus is aluminium.At first, with the molten metal processing of going bad, then be incubated 5-15min, carry out afterwards molten metal is poured into a mould, and extrusion head 1 presses down rapidly, arrive cover plate 3 places, guarantee that molten metal is at the liquid situation pressure set of property next time.Can rely on squeeze to make the feeding and solidifying by force of metal billet in this process, pressurize for some time, rise extrusion head 1, utilize push rod 8 slowly billet to be ejected.The related process parameter: the teeming temperature of liquid metal is 780 ℃, and die temperature is 300 ℃, extrusion speed 8mm/s, and specific pressure is 1000MPa, the dwell time is 40s, billet diameter of phi 70mm, height 100mm.
Take off the metal billet that has been shaped, except defining and peripheral oxide skin and impurity, integrated artistic flow process of the present invention as shown in Figure 6.In this course, due to the effect of pressure, make the coagulation equilibrium attitude destroyed, the alloy solid solution degree of Under Pressure Solidification has obtained expansion, and the pressure solidified structure is also nonequilibrium metastable phase, and the increase of its solid solubility is similar to rapid solidification.On the one hand, the molten metal temperature of solidification rises under pressure, and its result is exactly that matrix has begun forming core and grown up at also could not be able to do in time forming core and when growing up of alloying element, so just make alloying element be forced to be segmented in gap between matrix dendrite, form eutectic structure.On the other hand, also have a lot of alloying elements to be dissolved among matrix, make solid solubility rise, this point can be by being explained by spread coefficient and melt viscosity relation, to such an extent as to the billet that squeezes out has good plasticity.
Modification process is also key of the present invention in addition, and adding of alterant can form metal oxide or intermetallic compound particle as nucleus with a certain composition in aluminium alloy or impurity, and reduces the forming core merit, increases nucleation rate.The concrete composition of alterant can be different according to aluminium alloy and different, but have a unified principle to be:
Guarantee that its metamorphism has necessarily long-lasting, and there is no latent period;
For example, the strontium alterant acts on mutually to eutectic Si, changes its faller gill shape pattern, and adding content is the 0.02-0.06% of total mass; The effect of phosphor alterative primary Si phase changes its corner angle bulk morphologies, and adding content is the 0.5-1.5% of total mass.
Add method: can add with the master alloy form, also can be used as powder and be pressed into aluminium alloy and stir, can also add together with refining agent.
Below only with Al-17.5Si binary alloy squeeze cast form process explanation problem.
Be respectively the contrast of gravitational casting tissue as Fig. 2,3, obviously as seen, gravitational casting alloy structure, its Main Tissues are primary Si phase and eutectic Si phase constitution and Al matrix.Not rotten processing, as seen from Figure 2, primary Si phase is thick bulk, and out-of-shape and corner angle are distinct, and the Al matrix has been produced serious isolating, and seriously fall low-alloyed mechanical property, particularly plasticity.Eutectic Si is faller gill or lath-shaped mutually, and disorderly and unsystematic being distributed in the Al matrix is easy to produce stress concentration under force-bearing situation, causes formation of crack to generate, and reduces alloy property.And after adding Sr modification, as seen from Figure 3, primary Si phase remains thick bulk, with unmetamorphosed basic identical, but eutectic Si phase, noticeable change has but occured, the form that is eutectic Si phase has begun by the transformation of sheet to the branch shape, namely to the transformation of deteriorated structure, thereby, reduced stress concentration, the performance of alloy also is significantly increased.
Being respectively extrusion casting tissue contrast as Fig. 4,5, with the sample ingredient alloy, is that primary Si phase almost can not find by primary α-Al dendritic structure and eutectic Si mutually at the tissue of Under Pressure Solidification.Not rotten processing, as seen from Figure 4, the primary α-Al dendritic structure is very flourishing, and very intensive, be conducive to the raising of alloy property, eutectic Si becomes very thin lamellar by original faller gill or lath-shaped, thereby reduced the effect of isolating to its matrix, reduced issuable stress concentration in matrix, thereby the mechanical property of alloy is improved largely, especially plasticity has a very significant increase.And after adding Sr modification, as seen from Figure 5, the primary α-Al dendritic structure is still very flourishing, and very intensive, be conducive to equally the raising of alloy property, eutectic Si changes intensive tiny coralliform tissue into by original very thin lamellar, be distributed between dendrite, just because of this point, the mechanical property of alloy also has further raising, sees Table 1:
Table 1.
The below is the specific embodiment of the invention:
Embodiment 1:
The molten metal that step 2. utilizes tipper will go bad after processing injects mould by diversion trench, and the molten metal composition is by weight percentage: silicon 17.0%, copper 1.0%, magnesium 0.3%, nickel 0.5%, iron 0.5%, manganese 0.3%, chromium 0.5%, molybdenum 0.3%, phosphorus 0.07%, impurity summation≤0.5%, surplus are aluminium, before molten metal injects mould, mould need to be heated to 200 ℃, and scribbles coating on mould; When molten metal injected mould, the teeming temperature of molten metal was 690 ℃;
Embodiment 2:
The molten metal that step 2. utilizes tipper will go bad after processing injects mould by diversion trench, and the molten metal composition is by weight percentage: silicon 19.0%, copper 2.0%, magnesium 0.7%, nickel 1.0%, iron 1.0%, manganese 0.7%, chromium 1.0%, molybdenum 0.7%, phosphorus 0.15%, impurity summation≤0.5%, surplus are aluminium, before molten metal injects mould, mould need to be heated to 300 ℃, and scribbles coating on mould; When molten metal injected mould, the teeming temperature of molten metal was 780 ℃;
Embodiment 3:
The molten metal that step 2. utilizes tipper will go bad after processing injects mould by diversion trench, and the molten metal composition is by weight percentage: silicon 18.0%, copper 1.5%, magnesium 0.5%, nickel 0.8%, iron 0.7%, manganese 0.6%, chromium 0.8%, molybdenum 0.5%, phosphorus 0.1%, impurity summation≤0.5%, surplus are aluminium, before molten metal injects mould, mould need to be heated to 250 ℃, and scribbles coating on mould; When molten metal injected mould, the teeming temperature of molten metal was 750 ℃;
Embodiment 4:
The molten metal that step 2. utilizes tipper will go bad after processing injects mould by diversion trench, and the molten metal composition is by weight percentage: silicon 17.5%, copper 1.3%, magnesium 0.4%, nickel 0.6%, iron 0.9%, manganese 0.5%, chromium 0.6%, molybdenum 0.4%, phosphorus 0.09%, impurity summation≤0.5%, surplus are aluminium, before molten metal injects mould, mould need to be heated to 230 ℃, and scribbles coating on mould; When molten metal injected mould, the teeming temperature of molten metal was 700 ℃;
Embodiment 5:
The molten metal that step 2. utilizes tipper will go bad after processing injects mould by diversion trench, and the molten metal composition is by weight percentage: silicon 18.5%, copper 1.8%, magnesium 0.6%, nickel 0.7%, iron 0.8%, manganese 0.4%, chromium 0.9%, molybdenum 0.6%, phosphorus 0.12%, impurity summation≤0.5%, surplus are aluminium, before molten metal injects mould, mould need to be heated to 280 ℃, and scribbles coating on mould; When molten metal injected mould, the teeming temperature of molten metal was 770 ℃;
Embodiment 6:
The molten metal that step 2. utilizes tipper will go bad after processing injects mould by diversion trench, and the molten metal composition is by weight percentage: silicon 19%, copper 1.1%, magnesium 0.45%, nickel 0.9%, iron 0.6%, manganese 0.55%, chromium 0.7%, molybdenum 0.45%, phosphorus 0.14%, impurity summation≤0.5%, surplus are aluminium, before molten metal injects mould, mould need to be heated to 210 ℃, and scribbles coating on mould; When molten metal injected mould, the teeming temperature of molten metal was 730 ℃;
Claims (8)
1. rotten hypereutectic Al-Si alloy extrusion casting forming method of processing, it is characterized in that: described method is carried out according to following steps:
die tip is provided with the diversion trench that is connected with crucible, utilize tipper that molten metal is injected mould by diversion trench, the molten metal composition is by weight percentage: silicon 17.0～19.0%, copper 1.0～2.0%, magnesium 0.3～0.7%, nickel 0.5～1.0%, iron 0.5～1.0%, manganese 0.3～0.7%, chromium 0.5～1.0%, molybdenum 0.3～0.7%, phosphorus 0.07～0.15%, impurity summation≤0.5%, surplus is aluminium, and the extrusion head of extrusion machine is descended rapidly, begin molten metal is pressurizeed, make the feeding and solidifying by force of metal billet, through after pressurize, billet is taken out.
2. the rotten hypereutectic Al-Si alloy extrusion casting forming method of processing according to claim 1 is characterized in that: before molten metal injects mould, add alterant processings of go bad, be incubated 5-15min, and then pour into a mould.
3. go bad according to claim 2 and process hypereutectic Al-Si alloy extrusion casting forming method, it is characterized in that: alterant is strontium, add-on is the 0.02-0.06% of molten metal total mass, can add with the master alloy form, also can be used as powder and be pressed into molten metal and stir, can also add together with refining agent.
4. go bad according to claim 2 and process hypereutectic Al-Si alloy extrusion casting forming method, it is characterized in that: alterant is phosphorus, add-on is the 0.5-1.5% of molten metal total mass, can add with the master alloy form, also can be used as powder and be pressed into molten metal and stir, can also add together with refining agent.
5. go bad according to claim 1 and process hypereutectic Al-Si alloy extrusion casting forming method, it is characterized in that: before molten metal injected mould, mould need to be heated to 200～300 ℃, and scribbles coating on mould.
6. go bad according to claim 1 and process hypereutectic Al-Si alloy extrusion casting forming method, it is characterized in that: when molten metal injected mould, the teeming temperature of molten metal was 690～780 ℃.
7. go bad according to claim 1 and process hypereutectic Al-Si alloy extrusion casting forming method, it is characterized in that: the lowering speed of extrusion head is 0.1mm/s～12mm/s, and specific pressure is 70MPa～1500Mpa.
8. go bad according to claim 1 and process hypereutectic Al-Si alloy extrusion casting forming method, it is characterized in that: the dwell time is 10s～60s.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201110405443.5A CN103160717B (en) | 2011-12-08 | 2011-12-08 | A kind of rotten hypereutectic Al-Si alloy extrusion casting forming method of processing |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201110405443.5A CN103160717B (en) | 2011-12-08 | 2011-12-08 | A kind of rotten hypereutectic Al-Si alloy extrusion casting forming method of processing |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN103160717A true CN103160717A (en) | 2013-06-19 |
| CN103160717B CN103160717B (en) | 2016-05-04 |
Family
ID=48584247
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201110405443.5A Expired - Fee Related CN103160717B (en) | 2011-12-08 | 2011-12-08 | A kind of rotten hypereutectic Al-Si alloy extrusion casting forming method of processing |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN103160717B (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104139171A (en) * | 2014-08-09 | 2014-11-12 | 哈尔滨工业大学 | Gradient compounding pressure head device suitable for pressure casting technology |
| CN104480357A (en) * | 2014-12-05 | 2015-04-01 | 福州大学 | High-silicon aluminum alloy cylinder sleeve and preparation method thereof |
| CN105088024A (en) * | 2015-08-27 | 2015-11-25 | 华晨汽车集团控股有限公司 | Automobile welding fixture alloy material and preparation method thereof |
| CN106702228A (en) * | 2017-01-23 | 2017-05-24 | 沈阳工业大学 | Extrusion casting forming hypereutectic Al-Si alloy and preparation method thereof |
| CN111876637A (en) * | 2020-07-08 | 2020-11-03 | 上海永茂泰汽车科技股份有限公司 | Heat-resistant and wear-resistant Al-Si-Cu-Ni aluminum alloy and preparation method and application thereof |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1951605A (en) * | 2006-11-16 | 2007-04-25 | 上海交通大学 | Extrusion casting preparation method for aluminium alloy automobile engine bracket |
| CN101229582A (en) * | 2008-02-22 | 2008-07-30 | 昆明理工大学 | Semi-solid rheo-extrusion casting technology and equipment of hypereutectic Al-Si alloy casting |
| CN101560620A (en) * | 2009-05-27 | 2009-10-21 | 沈阳工业大学 | High strength heat-resisting hypereutectic aluminium-silicon alloy and preparation method thereof |
-
2011
- 2011-12-08 CN CN201110405443.5A patent/CN103160717B/en not_active Expired - Fee Related
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1951605A (en) * | 2006-11-16 | 2007-04-25 | 上海交通大学 | Extrusion casting preparation method for aluminium alloy automobile engine bracket |
| CN101229582A (en) * | 2008-02-22 | 2008-07-30 | 昆明理工大学 | Semi-solid rheo-extrusion casting technology and equipment of hypereutectic Al-Si alloy casting |
| CN101560620A (en) * | 2009-05-27 | 2009-10-21 | 沈阳工业大学 | High strength heat-resisting hypereutectic aluminium-silicon alloy and preparation method thereof |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104139171A (en) * | 2014-08-09 | 2014-11-12 | 哈尔滨工业大学 | Gradient compounding pressure head device suitable for pressure casting technology |
| CN104480357A (en) * | 2014-12-05 | 2015-04-01 | 福州大学 | High-silicon aluminum alloy cylinder sleeve and preparation method thereof |
| CN104480357B (en) * | 2014-12-05 | 2016-09-07 | 福州大学 | A kind of high-silicon aluminum alloy cylinder sleeve and preparation method thereof |
| CN105088024A (en) * | 2015-08-27 | 2015-11-25 | 华晨汽车集团控股有限公司 | Automobile welding fixture alloy material and preparation method thereof |
| CN106702228A (en) * | 2017-01-23 | 2017-05-24 | 沈阳工业大学 | Extrusion casting forming hypereutectic Al-Si alloy and preparation method thereof |
| CN111876637A (en) * | 2020-07-08 | 2020-11-03 | 上海永茂泰汽车科技股份有限公司 | Heat-resistant and wear-resistant Al-Si-Cu-Ni aluminum alloy and preparation method and application thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN103160717B (en) | 2016-05-04 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN105525158B (en) | A kind of semisolid pressure casting aluminum alloy materials and the method using the material die cast | |
| CN101439396B (en) | Counter-pressure casting process for casting parts of door cover | |
| CN102397905B (en) | Hot extrusion forming method for hypereutectic Al-Si alloy | |
| CN103160717B (en) | A kind of rotten hypereutectic Al-Si alloy extrusion casting forming method of processing | |
| CN103320651A (en) | Fine-grained zinc-based alloy for die and preparation process thereof | |
| CN102423798B (en) | A kind of hypereutectic Al-Si alloy extrusion casting forming method and mould thereof | |
| CN102994784B (en) | The method of phase constitution in high-intensity magnetic field compound modifier refinement transcocrystallized Al-Si alloy | |
| CN102965551A (en) | Hypereutectic aluminium-silicon alloy and preparation method thereof | |
| CN108290210A (en) | Method for manufacturing light metal casting component and light metal casting component | |
| CN112626390A (en) | High-elongation die-casting aluminum alloy and preparation method thereof | |
| CN104942271A (en) | Beryllium-aluminum alloy sheet and manufacturing method thereof | |
| CN102719688B (en) | Process method capable of improving thermal fatigue property of polynary zinc-aluminum alloy | |
| CN114438373A (en) | Bright anodized extrusion casting aluminum alloy and preparation method thereof | |
| CN103509979A (en) | Lubrication oil tank for excavating machine and manufacturing method thereof | |
| KR101110947B1 (en) | Method for producing metal matrix composite materials | |
| US4990310A (en) | Creep-resistant die cast zinc alloys | |
| Zyska et al. | Optimization of squeeze parameters and modification of AlSi7Mg alloy | |
| US4709461A (en) | Method of forming dense ingots having a fine equiaxed grain structure | |
| CN104060154A (en) | QT500 casting and production method thereof | |
| CN108728706A (en) | A kind of pressure casting method of auto parts machinery | |
| US20050126737A1 (en) | Process for casting a semi-solid metal alloy | |
| CN107523728A (en) | A kind of magnesium alloy and preparation method thereof | |
| CN106702228A (en) | Extrusion casting forming hypereutectic Al-Si alloy and preparation method thereof | |
| CN106756293A (en) | A kind of preparation method of ferro-silicon-aluminium copper magnesium alloy | |
| CN111842852A (en) | Method for preparing wear-resistant corrosion-resistant high-strength copper and copper alloy structural member by liquid die forging infiltration |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| TR01 | Transfer of patent right |
Effective date of registration: 20181119 Address after: 226300 Andong Village Group 2, Sian Town, Tongzhou District, Nantong City, Jiangsu Province Patentee after: Nantong Shuangyao Stamping Co., Ltd. Address before: 110870 No. 111 Shenyang West Road, Shenyang economic and Technological Development Zone, Liaoning Patentee before: Shenyang University of Technology |
|
| TR01 | Transfer of patent right | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20160504 Termination date: 20181208 |
|
| CF01 | Termination of patent right due to non-payment of annual fee |