CN100366782C - Aluminum-silicon alloys having improved mechanical properties - Google Patents

Aluminum-silicon alloys having improved mechanical properties Download PDF

Info

Publication number
CN100366782C
CN100366782C CNB028217861A CN02821786A CN100366782C CN 100366782 C CN100366782 C CN 100366782C CN B028217861 A CNB028217861 A CN B028217861A CN 02821786 A CN02821786 A CN 02821786A CN 100366782 C CN100366782 C CN 100366782C
Authority
CN
China
Prior art keywords
silicon
average
nodularization
alloy
phase component
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.)
Expired - Fee Related
Application number
CNB028217861A
Other languages
Chinese (zh)
Other versions
CN1602368A (en
Inventor
E·奥里斯
P·乌戈维策尔
J·沃雷尔
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Salzburger Aluminium AG
Original Assignee
Salzburger Aluminium AG
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Salzburger Aluminium AG filed Critical Salzburger Aluminium AG
Publication of CN1602368A publication Critical patent/CN1602368A/en
Application granted granted Critical
Publication of CN100366782C publication Critical patent/CN100366782C/en
Anticipated expiration legal-status Critical
Expired - Fee Related legal-status Critical Current

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/043—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with silicon as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • C22C21/04—Modified aluminium-silicon alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon

Abstract

The invention relates to a heat treatment method for articles composed of substantially Al-Si alloys that contain a eutectic phase, and to articles that consist of these alloys. In order to improve the ductility of the material or to increase the elongation after fracture, an annealing process is carried out in the form of shock annealing, said process comprising the following steps: rapidly heating the material to an annealing temperature of from 400 to 555 DEG C, maintaining it at this temperature for a period of not more than 14.8 minutes, force-cooling it, and then aging the article. The inventive article comprises spheroidized silicon precipitations in the eutectic phase portion with an average plane of section ASi of less than 4 mu m2 and/or an average distance between the silicon particles lambda Si of less than 4 mu m and/or an average spheroidization density xi Si of greater than 10.

Description

Aluminium-silicon-alloy that mechanical property is improved
The present invention relates to a kind of method that is used to improve aluminium-silicon-alloy mechanical performance.In particular, the present invention relates to a kind of heat treating method that improves object materials ductility, this object is made of cast alloys that has the eutectic phase component or plastic metal, it preferably contains modified (veredelten) or purified aluminium-element silicon, other alloying elements and/or impurity element are also randomly arranged, and this object then carries out the timeliness effect after anneal.
The invention still further relates to a kind of object, this object is to be made of the aluminium-silicon that has the eutectic phase component-alloy, it preferably has at least a modified element (Veredelungselement), randomly also contains magnesium and other alloys and/or impurity element, eutectic phase component wherein mainly by α- AlMatrix and silicon precipitation constitute.
Aluminium and silicon form a kind of simple eutectic system, and wherein, Si concentration is that eutectoid point appears when being 577 ℃ in 12.5 weight % and temperature.
By addition element magnesium and through thermal treatment and formed Mg 2Si precipitation can significantly improve the intensity of material, when magnesium is about 550 ℃ in temperature, can be dissolved in α- AlMaximum amount in the matrix is 0.47 weight %.
Can solidify to eutectic residual melt by cooling Al-Si-Mg melt, wherein silicon is with flaky thick form precipitation.Prior art for a long time is to mix sodium or strontium in this alloy, stops the growth of silicon crystal when solidifying thus, is referred to as modifiedly or refining, can improve mechanical property, particularly extension at break unlimitedly.
Basically can influence the mechanical property of aluminium alloy work in-process or object by heat treating method, by European standard EN515 definition as-heat-treated condition.According to standard, in steady state letter F=production status, T=is heat treated.The numerical table that each as-heat-treated condition is arranged after by tee shows.
In addition, below represent the following as-heat-treated condition of material with dummy suffix notation in the explanation:
F is a production status
T5 is from the quenching of production temperature and carries out the thermal life effect
T6 is liquation annealing and carries out the thermal life effect
T6x is according to thermal treatment of the present invention
T4x is according to thermal treatment of the present invention
When using the object that constitutes by the Al-Si alloy for being fit to market demand or industry, material property is important on the one hand, but production cost or economic conditions also are important on the other hand, because anneal under high temperature more for a long time, and essential during long term annealing to pass through the indispensable aligning process (Nachrichtvorg  nge) that so-called gravity creep carries out be expensive.
Basically can confirm that the Al-Si alloy of F state has little strength of materials value R mostly pWith higher extension at break coefficient A.
At as-heat-treated condition T5, i.e. the quenching of production temperature and carry out the thermal life effect is for example in the time of 155 ℃ to 190 ℃, during 1 to 12 hour, though reach the intensity level R of sample pHigher, but extension at break coefficient A is lower.
The as-heat-treated condition of corresponding T6, promptly for example liquation carries out the thermal life effect subsequently 540 ℃ of annealing temperatures 12 hours, and F compares with state, and under the situation that the ductility of the extension at break of sample or material equates substantially, but the intensity of material improves greatly.For example, the liquation annealing time is long, and the magnesium atom in the material is advantageously spread, therefore, after object quenching and thermal life are used, α- AlForm the Mg that distributes very evenly in the matrix 2The Si precipitation, this precipitation improves the strength of materials fatefully.
But, during high temperature liquation is carried out long term annealing and handle the shortcoming that exists, as mentioned above, i.e. Bu Fen gravitational creep and expensive temperature-time degree of treatment.Therefore, from economically, many-sided consideration on the maximum intensity that reaches material and the good ductility is not selected T6, and is selected the treated state T5 of object.Randomly must compensate the low strength of materials that determines because of T5 by the structure that changes member.
At this situation, the invention provides a kind of novel, economic heat treating method, this method can significantly improve the ductility of material, compare with T6, the strength of materials is not had big interference, perhaps compare, obtain showing the higher ductility and the higher strength of materials with T5.
In addition, the purpose of this invention is to provide a kind of microtexture that begins the object of the favourable mechanical property of materials of having of described class.
The purpose of present method is achieved in that promptly with impact type annealing carries out the liquation anneal, comprising: being heated rapidly to 400-555 ℃ annealing temperature, is 14.8 minutes in the soaking time the longest of this temperature, forces to be cooled to room temperature basically then.
Advantage of the present invention mainly is, adopts simple high temperature-short annealing to reach the ductility value of object maximum.In addition, so-called impact type anneal makes the deformation of member or deformation of body reduce so randomly not need self aligning up to not taking place.Anneal also has higher economic value rapidly, and can for example by continuous furnace, incorporate in the production process with plain mode.At least can regulate the strength of materials by a kind of adjusting process of thermal life effect subsequently.Be less than 6.8 minutes if can be advantageously provided the hold-time of impact type anneal, preferred 1.7 to randomly maximum 5 minutes, then improves ductility to greatest extent under the dominant situation of the quantity of Al-Si alloy.
Carry out the thermal life effect of object after the impact type annealing, being about to it, to place 1-14 hour under 150-200 ℃ of temperature be favourable.
If impact type annealing back also is favourable to material technology then carrying out the timeliness effect of object under the room temperature with the cold ageing effect substantially.
Another object of the present invention is such realization, though the nodularization of the silicon of eutectic phase component precipitation, its average cross section A SiLess than 4 μ m 2
Below the formula in cross section is calculated in expression,
A Si = 1 n Σ k = 1 n A ≤ 4 μm 2
Parametric representation wherein:
A SiThe average area of=silicon particle (μ m 2)
The average area of the silicon particle of every photo of A=(μ m 2)
N=measures number of times
The advantage of this microtexture mainly is, because sedimentary nodularization of silicon and purifying have reduced the initial crack of material basically, and improved material ductility.In other words, nodularization and small size make brittle eutectic silicon have suitable form, fundamentally cause the higher extension at break value of material.Stress concentration when having reduced mechanical load on the Si-Al phase interface.Also find the transgranular fracture of material in the test, therefore demonstrate the highest ductility.
If the silicon of eutectic phase component precipitation is nodularization, and average cross section is less than 2 μ m 2, then the high extension at break value for complete processing and material is favourable.
Pointed as R﹠D work, if be implemented as follows the present invention, promptly be defined as foursquare survey area divided by the mean free path λ between the silicon particle of the eutectic phase component of the root of the number of its contained silicon particle according to goal of the invention SiValue less than 4 μ m, preferably less than 3 μ m, especially preferably, then when minimum peak stress, reach special uniform stress distribution in the material of load, because the spacing of small area silicon particle has mainly influenced the rheological property of material under the corresponding stressed condition less than 2 μ m.Calculate the average headway λ of silicon particle once more with following formula Si
Figure C0282178600081
λ SiThe average headway of=silicon particle
A Square=foursquare reference plane (μ m 2)
N SiliconThe number of=Si particulate
N=measures the number of photo
The liquation annealing of prior art is the long term annealing at 2 to 12 hours, so that the alloy compositions diffusion of sclerization is arranged, and be enriched in the mixed crystal, though also cause the side effect of nodularization silicon particle, but because annealing for a long time, these Particle Distribution are very big and coarse, and this fracture property to material is unfavorable.According to the present invention, surprisingly,, can in the short period of time of several minutes, make eutectic silicon crystal lattice nodularization, thereby obtain favourable material microstructure by impact type annealing rapidly.At this, importantly impact type annealed temperature should be high as far as possible, but should be lower than minimum fusion phase temperature, preferably low 5 to 20 ℃.
Make silicon particle carry out the growth of controlled diffusion with the prolongation annealing time, make originally favourable high nodularization density ξ this moment SiDiminished.
Find when realizing the object of the invention, if be defined as per 100 μ m 2The average nodularization density ξ of the number of the eutectic silicon particle of nodularization SiGreater than 10, and preferred 20, and then the ductility of Al-Si alloy object is the highest.
ξ Si = 1 n Σ k = 1 n N Si A × 100 ≥ 10
ξ SiThe average nodularization density of=eutectic silicon particle
N SiliconThe number of=Si particulate
A=reference plane (μ m 2)
N=measures the number of photo
Related formula explanation as previously mentioned.
The result shows that the every kind of Al-Si alloy that contains the eutectic phase basically all can have structure of the present invention, and the object of Xing Chenging has high material ductility value thus.If be equipped with object, all be effective especially then to improving quality and improving extension at break with the thixo casting legal system.
Further specify the present invention by test result and photo below:
Fig. 1 bar graph: the mechanical value that depends on the material of as-heat-treated condition
Fig. 2 is same
The REM photo of Fig. 3 section
Fig. 4 is same
The relation of sedimentary average area of Fig. 5 Si and annealing time
Fig. 6 is same
Mean free path between Fig. 7 Si particulate
The average nodularization density of Fig. 8
Fig. 9 bar graph: the mechanical property of the material of different al-Si alloy
The numerical value of table 1 Fig. 9
Table 1
F T5 T6×3 T6
Scheme Rp[MPa] A[％] Rp[MPa] A[％] Rp[MPa] A[％] Rp[MPa] A[％]
Alsi7Mg03 121.7 13.0 167.5 9.9 228.5 16.7 259.8 10.6
Alsi7Mg05 143.9 10.4 175.8 9.3 240.2 13.9 311.7 9.1
Alsi7Mgx 159.8 8.3 197.2 6.8 265.2 10.1 322.9 7.6
Alsi6Mgx 159.7 10.2 195.3 7.8 250.6 8.9 318.6 6.5
Alsi5Mgx 154.9 10.1 189.6 7.5 240.6 9.5 313.6 8.7
+Mn04 157.1 10.6 183.7 6.9 252.7 7.4 322.7 7.6
+Mn08 154.8 9.9 184.0 6.6 255.9 6.7 324.4 4.9
AlSi5Mgxx 211.7 3.5 256.4 2.5 242.1 5.1 291.6 5.3
Fig. 1 represents the R of the sample of the test component that made by alloy A lSi7Mg0.3 with bar graph P0.2Yield point value and extension at break value A, this alloy component prepares with thixo casting (Thixocastingverfahren).The value of material hot treatment state T6 (12 hours 540 ℃+4 hours 160 ℃) is compared in 1 minute (T6x1) back of 540 ℃ of following impact types annealing, 3 minutes (T6x3) back and T6x of obtaining after (T6x5) in 5 minutes with adopting the inventive method.All sample carries out thermal life effect (4 hours) under 160 ℃.Tensile test result shows that the extension at break value of the sample after the impact type anneal is obviously higher, compares with T6, and state T6x3 causes A to raise about 60%.
The state value that has compared the sample of same manufacturing once more with bar graph among Fig. 2 is the R of F, T4x3, T5, T6x3 and T6 P0.2With extension at break A.Show that more once more the extension at break value obviously raises.As can be seen from Figure 2, in order to obtain outstanding extension at break performance of the present invention, impact type annealing is after 3 minutes, cold ageing effect (T4x3) or the thermal life effect (T6x3) that can carry out material.
Fig. 3 and Fig. 4 represent the sedimentary electron scanning micrograph of Si.Note image pickup method and evaluation method:, must use suitable binary photo for can quantitative evaluation Photomicrograph (Schliffbilder).Take with scanning electronic microscope, reach 2 hours up to annealing time, the solution with 99.5% water and 0.5% hydrofluoric acid corroded abrasive disc 30 seconds in advance afterwards.Anneal after 4 hours, corrode abrasive disc with Keller solution, and with optics microscope photographing photo.All photos are with Adobe Photoshop 5.0 progressive number aftertreatments, and with picture analyzing program Leica Qwin V2.2 evaluation, wherein Zui Xiao area of detection is 0.1 μ m 2Fig. 3 shows the materials A lSi7Mg0.3 of conventional T6-annealing after 12 hours that takes with REM.Fig. 4 provides the microtexture of the material of impact type anneal after 3 minutes again.Silicon precipitation obviously nodularization (Fig. 4) after short period of time, behind the long annealing time self controlled diffusion grow (Fig. 3) be conspicuous.
Fig. 5 and Fig. 6 depend on the silicon particle average cross section A of 540 ℃ of following annealing times when representing the abrasive disc test SiDescription according to Fig. 4 can obviously find out, the average cross section of silicon particle that with the particle size is feature is along with logarithmic time shaft increases.From the detailed description of Fig. 6, can observe the increase of the average silicon area that in initial 60 minutes, causes owing to diffusion.Depend primarily on the initial size of Si particulate in the eutectic mixture along with the silicon particle mean sizes of annealing time increase.Owing to there is the special good modified silicon that distributes with purification under described situation, accidental can shorten the time under the modified not so good situation of silicon particle (particulate is bigger when showing beginning), interior crucial average silicon area A of this time SiReach about 4 μ m 2
The test-results of Fig. 7 represents to depend on the variation of average headway of the Si particulate of annealing time.The average headway that can obviously observe the Si inclusion increases.
At last, Fig. 8 represents to depend on the average nodularization density ξ of annealing time SiDecline.Average nodularization density has begun rapid decline in the time of 1.7 minutes, from value ξ Si＜10 are caused tangible ductility loss.During higher anneal temperature, just reach this value after 14 to 25 minutes, for dominant high extension at break value, density value is predetermined greater than 20.
Fig. 9 provides the elongation border of described 8 the different Al-Si alloys of forming of table 1 and the observed value of extension at break again by bar graph.The material ductility of all alloys of the present invention has all increased.
In sum, part technical scheme provided by the invention is as follows:
1. heat treating method that is used to improve the material ductility of object, this object is made of cast alloys with eutectic phase component or plastic metal, this alloy preferably contains modified or purified aluminium-element silicon, other are also randomly arranged such as magnesium, manganese, alloying element and/or impurity elements such as iron, this object then carries out the timeliness effect after anneal, it is characterized in that, carry out anneal with impact type annealing, it comprises: be heated rapidly to 400-555 ℃ annealing temperature, be preferably at least 1.7 minutes to maximum 14.8 minutes in this following hold-time of temperature, force to be cooled to room temperature basically subsequently.
2. according to the method for technical scheme 1, it is characterized in that the hold-time of impact type anneal, preferred time range was at least 1.7 minutes to randomly maximum 5 minutes less than 6.8 minutes.
3. according to the method for technical scheme 1 or 2, it is characterized in that, under 150 to 200 ℃ temperature, object was carried out the thermal life effect 1-14 hour after the impact type anneal.
4. according to the method for technical scheme 1 or 2, it is characterized in that, after the impact type annealing, under the room temperature object is being carried out the cold ageing effect basically.
5. object that forms by aluminum-silicon alloy with eutectic phase component, this alloy preferably has at least a modified element, randomly also has other such as alloying element and/or impurity elements such as magnesium, manganese, iron, this object mainly by α- AlMatrix and silicon precipitation constitute, and it is characterized in that, the silicon precipitation in the eutectic phase component is nodularization, its average cross section A SiLess than 4 μ m 2
A Si = 1 n Σ k = 1 n A ≤ 4 μm 2
A SiThe average area of=silicon particle (μ m 2)
The average area of the silicon particle of every photo of A=(μ m 2)
N=measures number of times.
6. according to the object of technical scheme 5, it is characterized in that the silicon precipitation in the eutectic phase component is nodularization, average cross section A SiLess than 2 μ m 2
7. object that forms by aluminum-silicon alloy with eutectic phase component, this alloy preferably has at least a modified element, randomly also has other such as alloying element and/or impurity elements such as magnesium, manganese, iron, this object mainly by α- AlMatrix and silicon precipitation constitute, and it is characterized in that, are defined as foursquare survey area divided by the mean free path λ between the silicon particle of the eutectic phase component of the root of the number of its contained silicon particle SiValue less than 4 μ m
Figure C0282178600131
λ SiThe average headway of=silicon particle
A Square=foursquare reference plane (μ m 2)
N SiliconThe number of=Si particulate
N=measures the number of photo.
8. according to the object of technical scheme 7, it is characterized in that the value of mean free path is less than 3 μ m, preferably less than 2 μ m.
9. object that constitutes by aluminum-silicon alloy with eutectic phase component, this alloy preferably has at least a modified element, randomly also has other such as alloying element and/or impurity elements such as magnesium, manganese, iron, this object mainly by α- AlMatrix and silicon precipitation constitute, and it is characterized in that, are defined as per 100 μ m 2The average nodularization density ξ of the number of the eutectic silicon particle of nodularization SiGreater than 10
ξ Si = 1 n Σ k = 1 n N Si A × 100 ≥ 10
ξ SiThe average nodularization density of=eutectic silicon particle
N SiliconThe number of=Si particulate
A=reference plane (μ m 2)
N=measures the number of photo.
10. according to the object of technical scheme 9, it is characterized in that the value of average nodularization density is greater than 20.
11. the object of one of technical scheme 5-10 or the object for preparing according to technical scheme 1-4 is characterized in that it prepares with the thixo casting method.

Claims (17)

1. heat treating method that is used to improve the material ductility of object, this object is made of cast alloys with eutectic phase component or plastic metal, this object then carries out the timeliness effect after anneal, it is characterized in that, carry out anneal with impact type annealing, it comprises: be heated rapidly to 400-555 ℃ annealing temperature, this following hold-time of temperature at least 1.7 minutes to maximum 14.8 minutes, force cool to room temperature subsequently.
2. according to the process of claim 1 wherein, this alloy contains modified or purified aluminium-element silicon, also randomly contains other alloying elements and/or impurity element.
3. according to the method for claim 2, wherein, this alloy randomly contains other alloying element that is selected from magnesium, manganese and iron and/or impurity elements.
4. according to the method for claim 1, it is characterized in that the hold-time of impact type anneal was less than 6.8 minutes.
5. according to the method for claim 1, it is characterized in that the hold-time scope of impact type anneal is at least 1.7 minutes to maximum 5 minutes.
6. according to the method for one of claim 1-5, it is characterized in that, under 150 to 200 ℃ temperature, object was carried out the thermal life effect 1-14 hour after the impact type anneal.
7. according to the method for one of claim 1-4, it is characterized in that, after the impact type annealing, at room temperature object is carried out the cold ageing effect.
8. according to the method for claim 5, it is characterized in that, after the impact type annealing, at room temperature object is carried out the cold ageing effect.
9. object that forms according to the aluminum-silicon alloy by having the eutectic phase component of the method for one of claim 1-8 preparation, this object mainly by α- AlMatrix and silicon precipitation constitute, and it is characterized in that, the silicon precipitation in the eutectic phase component is nodularization, its average cross section A SiIn 4 μ m 2:
A Si = 1 n Σ k = 1 n A ≤ 4 μ m 2
A SiThe average area of=silicon particle, it is with μ m 2Be unit
The average area of the silicon particle of every photo of A=, it is with μ m 2Be unit
N=measures number of times.
10. according to the object of claim 9, it is characterized in that the silicon precipitation in the eutectic phase component is nodularization, average cross section A SiIn 2 μ m 2
11. an object that forms according to the aluminum-silicon alloy by having the eutectic phase component of the method for one of claim 1-8 preparation, this object mainly by α- AlMatrix and silicon precipitation constitute, and it is characterized in that, are defined as foursquare survey area divided by the mean free path λ between the silicon particle of the eutectic phase component of the root of the number of its contained silicon particle SiValue less than 4 μ m:
λ SiThe average headway of=silicon particle
A Square=foursquare reference plane, it is with μ m 2Be unit
N SiliconThe number of=Si particulate
N=measures the number of photo.
12. the object according to claim 11 is characterized in that, the value of mean free path is less than 3 μ m.
13. an object that constitutes according to the aluminum-silicon alloy by having the eutectic phase component of the method for one of claim 1-8 preparation, this object mainly by α- AlMatrix and silicon precipitation constitute, and it is characterized in that, are defined as per 100 μ m 2The average nodularization density ξ of the number of the eutectic silicon particle of nodularization SiGreater than 10:
ξ Si = 1 n Σ k = 1 n N Si A × 100 ≥ 10
ξ SiThe average nodularization density of=eutectic silicon particle
N SiThe number of=Si particulate
The A=reference plane, it is with μ m 2Be unit
N=measures the number of photo.
14. the object according to claim 13 is characterized in that, the value of average nodularization density is greater than 20.
15. according to the object of one of claim 9-14, wherein, described alloy contains modified or purified aluminium-element silicon, also randomly contains other alloying elements and/or impurity element.
16. according to the object of claim 15, wherein, described alloy randomly contains other alloying element that is selected from magnesium, manganese and iron and/or impurity elements.
17., it is characterized in that it prepares with the thixo casting method according to the object of one of claim 9-14 or according to the object of the method preparation of one of claim 1-8.
CNB028217861A 2001-11-05 2002-11-05 Aluminum-silicon alloys having improved mechanical properties Expired - Fee Related CN100366782C (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
AT0173301A AT411269B (en) 2001-11-05 2001-11-05 ALUMINUM-SILICON ALLOYS WITH IMPROVED MECHANICAL PROPERTIES
ATA1733/2001 2001-11-05

Publications (2)

Publication Number Publication Date
CN1602368A CN1602368A (en) 2005-03-30
CN100366782C true CN100366782C (en) 2008-02-06

Family

ID=3688773

Family Applications (1)

Application Number Title Priority Date Filing Date
CNB028217861A Expired - Fee Related CN100366782C (en) 2001-11-05 2002-11-05 Aluminum-silicon alloys having improved mechanical properties

Country Status (15)

Country Link
US (2) US20050000608A1 (en)
EP (1) EP1442150B1 (en)
JP (1) JP2005508446A (en)
KR (1) KR20050043748A (en)
CN (1) CN100366782C (en)
AT (2) AT411269B (en)
CA (1) CA2465683C (en)
DE (1) DE50209192D1 (en)
DK (1) DK1442150T3 (en)
ES (1) ES2280578T3 (en)
HK (1) HK1071171A1 (en)
HU (1) HUP0401962A2 (en)
PT (1) PT1442150E (en)
SI (1) SI1442150T1 (en)
WO (1) WO2003040423A1 (en)

Families Citing this family (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US8950468B2 (en) 2007-05-11 2015-02-10 The Boeing Company Cooling system for aerospace vehicle components
DE102008024524A1 (en) * 2008-05-21 2009-11-26 Bdw Technologies Gmbh Method and plant for producing a cast component
DE102011105447B4 (en) * 2011-06-24 2019-08-22 Audi Ag Process for the production of aluminum die-cast parts
CN107586939A (en) * 2017-09-13 2018-01-16 中信戴卡股份有限公司 A kind of heat treatment method for aluminium alloy casting rotation wheel
CN109706411A (en) * 2019-02-18 2019-05-03 东莞宏幸智能科技有限公司 A kind of solid smelting furnace of aluminum alloy spare part production
CN115961223A (en) * 2022-12-19 2023-04-14 湖南中创空天新材料股份有限公司 Method for removing residual stress

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH05263203A (en) * 1992-03-17 1993-10-12 Sky Alum Co Ltd Production of rolled sheet of aluminum alloy for forming
JPH07166285A (en) * 1993-06-08 1995-06-27 Shinko Alcoa Yuso Kizai Kk Hardened al alloy sheet by baking and production thereof
JPH11613A (en) * 1997-06-13 1999-01-06 Kawasaki Steel Corp Manufacture of aluminum alloy plate with superior molding properties and coat baking/curing properties
CN1221047A (en) * 1997-11-18 1999-06-30 Ina滚柱轴承制造两合公司 Aluminium-silicon casted alloy construction member
EP1057900A1 (en) * 1999-06-04 2000-12-06 VAW Aluminium AG Cast cylinder head and block

Family Cites Families (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5985349A (en) * 1998-11-12 1999-11-16 Kraft Foods, Inc. Method for manufacture of grated cheese
DE19901508A1 (en) * 1999-01-16 2000-08-17 Bayerische Motoren Werke Ag Process for the production of castings from aluminum alloys
JP2001316747A (en) * 1999-08-31 2001-11-16 Asahi Tec Corp NON-Cu CAST Al ALLOY AND HEAT TREATING METHOD THEREFOR
JP3857503B2 (en) * 2000-07-26 2006-12-13 大同メタル工業株式会社 Aluminum bearing alloy
EP1468245B1 (en) * 2002-01-11 2011-03-30 The General Hospital Corporation Apparatus for OCT imaging with axial line focus for improved resolution and depth of field

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH05263203A (en) * 1992-03-17 1993-10-12 Sky Alum Co Ltd Production of rolled sheet of aluminum alloy for forming
JPH07166285A (en) * 1993-06-08 1995-06-27 Shinko Alcoa Yuso Kizai Kk Hardened al alloy sheet by baking and production thereof
JPH11613A (en) * 1997-06-13 1999-01-06 Kawasaki Steel Corp Manufacture of aluminum alloy plate with superior molding properties and coat baking/curing properties
CN1221047A (en) * 1997-11-18 1999-06-30 Ina滚柱轴承制造两合公司 Aluminium-silicon casted alloy construction member
EP1057900A1 (en) * 1999-06-04 2000-12-06 VAW Aluminium AG Cast cylinder head and block

Also Published As

Publication number Publication date
DK1442150T3 (en) 2007-05-14
KR20050043748A (en) 2005-05-11
DE50209192D1 (en) 2007-02-15
AT411269B (en) 2003-11-25
ES2280578T3 (en) 2007-09-16
WO2003040423A1 (en) 2003-05-15
CA2465683A1 (en) 2003-05-15
US20100193084A1 (en) 2010-08-05
CN1602368A (en) 2005-03-30
SI1442150T1 (en) 2007-06-30
HK1071171A1 (en) 2005-07-08
ATA17332001A (en) 2003-04-15
HUP0401962A2 (en) 2005-01-28
EP1442150A1 (en) 2004-08-04
PT1442150E (en) 2007-04-30
CA2465683C (en) 2011-01-18
US20050000608A1 (en) 2005-01-06
JP2005508446A (en) 2005-03-31
EP1442150B1 (en) 2007-01-03
ATE350507T1 (en) 2007-01-15

Similar Documents

Publication Publication Date Title
KR101148421B1 (en) Aluminum alloy forgings and process for production thereof
EP3009525A1 (en) Aluminium alloy forging and method for producing the same
KR100831637B1 (en) Aluminum alloy sheet having excellent formability and paint bake hardenability
JP5031971B2 (en) Aluminum-based alloys and methods for producing workpieces thereof
JP5343333B2 (en) Method for producing high-strength aluminum alloy material with excellent resistance to stress corrosion cracking
Tsuya et al. On the effects of vacuum annealing and carburizing on the ductility of coarse-grained molybdenum
Tan Influence of Heat Treatment on the Mechanical Properties of AA6066 Alloy.
CA1113283A (en) Heat resistant low expansion alloy
EP0008996B1 (en) Process for heat-treating aluminium-copper-magnesium-silicon alloys
EP0480402A1 (en) Process for manufacturing aluminium alloy material with excellent formability, shape fixability and bake hardenability
JP2001517735A (en) Aluminum alloy and heat treatment method thereof
Kaiser Effect of Solution Treatment on the Age-Hardening Behavior of Al-12Si-1Mg-1Cu Piston Alloy with Trace-Zr Addition
US20100193084A1 (en) Aluminum-silicon alloys having improved mechanical properties
JP3721020B2 (en) High strength, high toughness aluminum alloy forging with excellent corrosion resistance
JP2004269994A (en) BIOCOMPATIBLE Co BASED ALLOY, AND PRODUCTION METHOD THEREFOR
JPS58167757A (en) Preparation of al-mg-si alloy for processing excellent in corrosion resistance, weldability and hardenability
US20230357902A1 (en) Method For Manufacturing Aluminum Alloy Extruded Material With High Strength And Excellent In SCC Resistance And Hardenability
JP3516566B2 (en) Aluminum alloy for cold forging and its manufacturing method
JPH06340940A (en) Aluminum alloy sheet excellent in press formability and baking hardenability and its production
CN106167879B (en) Maraging steel
JP6536317B2 (en) α + β-type titanium alloy sheet and method of manufacturing the same
JP2007509240A (en) Al-Mg-Si alloy suitable for extrusion
JP3633907B2 (en) High tensile cast steel and method for producing the same
JP3498943B2 (en) Al-Mg-Si-based aluminum alloy sheet for forming with excellent surface properties
JPH01501325A (en) Aluminum-lithium alloy and its manufacturing process

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
C17 Cessation of patent right
CF01 Termination of patent right due to non-payment of annual fee

Granted publication date: 20080206

Termination date: 20121105