WO2018162823A1 - Elements de chambres a vide en alliage d'aluminium stables a haute temperature - Google Patents
Elements de chambres a vide en alliage d'aluminium stables a haute temperature Download PDFInfo
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- WO2018162823A1 WO2018162823A1 PCT/FR2018/050481 FR2018050481W WO2018162823A1 WO 2018162823 A1 WO2018162823 A1 WO 2018162823A1 FR 2018050481 W FR2018050481 W FR 2018050481W WO 2018162823 A1 WO2018162823 A1 WO 2018162823A1
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- 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
- C22F1/05—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 of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions
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- 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
-
- 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
- C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
- C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
-
- 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
- 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
- C22F1/047—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 magnesium as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
- C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
- C25D11/00—Electrolytic coating by surface reaction, i.e. forming conversion layers
- C25D11/02—Anodisation
- C25D11/04—Anodisation of aluminium or alloys based thereon
-
- C—CHEMISTRY; METALLURGY
- C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
- C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
- C25D11/00—Electrolytic coating by surface reaction, i.e. forming conversion layers
- C25D11/02—Anodisation
- C25D11/04—Anodisation of aluminium or alloys based thereon
- C25D11/06—Anodisation of aluminium or alloys based thereon characterised by the electrolytes used
- C25D11/08—Anodisation of aluminium or alloys based thereon characterised by the electrolytes used containing inorganic acids
-
- C—CHEMISTRY; METALLURGY
- C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
- C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
- C25D11/00—Electrolytic coating by surface reaction, i.e. forming conversion layers
- C25D11/02—Anodisation
- C25D11/04—Anodisation of aluminium or alloys based thereon
- C25D11/06—Anodisation of aluminium or alloys based thereon characterised by the electrolytes used
- C25D11/10—Anodisation of aluminium or alloys based thereon characterised by the electrolytes used containing organic acids
-
- C—CHEMISTRY; METALLURGY
- C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
- C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
- C25D11/00—Electrolytic coating by surface reaction, i.e. forming conversion layers
- C25D11/02—Anodisation
- C25D11/04—Anodisation of aluminium or alloys based thereon
- C25D11/18—After-treatment, e.g. pore-sealing
Definitions
- the invention relates to aluminum alloy products for use as vacuum chamber elements in particular for the manufacture of integrated electronic circuits based on semiconductors, flat display screens and photovoltaic panels and their use. manufacturing process.
- Vacuum chamber elements for the fabrication of integrated electronic circuits based on semiconductors, flat display screens as well as photovoltaic panels, can typically be obtained from aluminum alloy sheets.
- the vacuum chamber elements are elements for the manufacture of vacuum chamber structures and internal vacuum chamber components including vacuum chamber bodies, valve bodies, flanges, connection elements, elements sealing, passages, diffusers, electrodes. They are obtained in particular by machining and surface treatment of aluminum alloy sheets.
- the aluminum alloy sheets must have certain properties.
- the sheets must first have satisfactory mechanical characteristics to achieve by machining parts having the desired dimensions and rigidity so as to achieve, without deformation, a vacuum generally at least the level of the average vacuum (10 ⁇ 3 -.. 10 "5 Torr)
- tensile strength (R m) desired is generally at least 260 MPa and even more if possible in addition, to be suitable for machining the sheets intended to be machined in the mass must have homogeneous properties in the thickness and have a low density of stored elastic energy from the residual stresses.
- the vacuum chamber elements are subjected to high temperatures and it is important that their resistance to creep deformation at high temperature is important.
- the level of porosity of the sheets must also be sufficiently low to reach if necessary the high-vacuum (10 ⁇ 6 - 10 "8 Torr).
- vacuum chambers are frequently very corrosive and so as to avoid the risk of pollution of silicon wafers or liquid crystal devices by particles or substances from vacuum chamber elements and / or frequent replacement of these elements, It is important to protect the surfaces of the vacuum chamber elements.
- Aluminum proves to be an advantageous material from this point of view because it is possible to perform a surface treatment generating an oxide layer resistant to reactive gases. This surface treatment comprises an anodizing step and the oxide layer obtained is generally called anodic layer.
- corrosion resistance the resistance of the anodized aluminum corrosive gases used in the vacuum chambers and corresponding tests.
- the corrosion resistance is evaluated in particular by the test called “bubble test” which consists of measuring the duration of appearance of hydrogen bubbles on the surface of the anodized product when in contact with a dilute hydrochloric acid solution.
- bubble test The known times in the state of the art are of the order of tens of minutes to a few hours.
- vacuum chamber elements can be improved aluminum sheets and / or the surface treatment performed.
- US Pat. No. 6,713,188 discloses an alloy suitable for manufacturing chambers for semiconductor manufacturing of composition (in% by weight) Si: 0.4 - 0.8; Cu: 0.15-0.30; Fe: 0; 001 - 0; 20; Mn 0.001 - 0.14; Zn 0.001 - 0.15; Cr: 0.04 - 0.28; Ti 0.001 - 0.06; Mg: 0.8 - 1.2.
- the pieces are obtained by extrusion or machining to the desired shape.
- the composition makes it possible to control the size of the impurity particles, which improves the performance of the anodic layer.
- US Pat. No. 7,033,447 claims an alloy suitable for manufacturing chambers for semiconductor manufacturing of composition (in% by weight) Mg: 3.5-4.0; Cu: 0.02 - 0.07; Mn: 0; 005-0; 015; Zn 0.08 - 0.16; Cr 0.02 - 0.07; Ti: 0 - 0.02; If ⁇ 0.03; Fe ⁇ 0.03.
- the parts are anodized in a solution comprising 10% to 20% by weight of sulfuric acid, 0.5 to 3% by weight of oxalic acid at a temperature of 7 to 21 ° C. The best result obtained in the bubble test is 20 hours.
- US Patent 6,686,053 claims an alloy having improved corrosion resistance, wherein the anodic oxide comprises a barrier layer and a porous layer and wherein at least a portion of the layer is altered to boehmite and / or pseudo-boehmite.
- the best result obtained in the bubble test is of the order of 10 hours.
- US Patent Application 2009/0050485 discloses a composition alloy (in% by weight) Mg: 0.1 - 2.0; If: 0.1 - 2.0; Mn: 0.1 - 2.0; Fe, Cr, and Cu ⁇ 0.03, anodized so that the hardness of the anodic oxide layer varies in thickness.
- the very low content of iron, chromium and copper leads to a significant additional cost for the metal used.
- US Patent Application 2010/0018617 discloses a composition alloy (in% by weight) Mg: 0.1 - 2.0; If: 0.1 - 2.0; Mn: 0.1 - 2.0; Fe, Cr, and Cu ⁇ 0.03, the alloy being homogenized at a temperature of greater than 550 ° C to 600 ° C or less.
- the international application WO2011 / 89337 (Constellium) describes a process for producing non-rolled cast products suitable for the manufacture of vacuum chamber elements of composition, in% by weight, Si: 0.5 - 1.5; Mg: 0.5 - 1.5; Fe ⁇ 0.3; Cu ⁇ 0.2; Mn ⁇ 0.8; Cr ⁇ 0.10; Ti ⁇ 0.15.
- US Patent 6,066,392 discloses an aluminum material having anodic oxidation film with improved corrosion resistance, wherein cracks are not generated even in high temperature thermal cycles and in environments corrosive.
- US Patent 6,027,629 discloses an improved surface treatment method for vacuum chamber elements in which the pore diameter of the anode layer is variable in the thickness thereof.
- US Pat. No. 7,005,194 discloses an improved surface treatment method for vacuum chamber elements in which the anodized film is composed of a porous layer and a non-porous layer whose structure is at least partly boehmite or pseudo-boehmite.
- the patent application WO2014 / 060660 (Constellium France) relates to a vacuum chamber element obtained by machining and surface treatment of a sheet of thickness at least equal to 10 mm aluminum alloy composition, in% by weight , Si: 0.4 - 0.7; Mg: 0.4 - 0.7; Ti 0.01 - ⁇ 0.15, Fe ⁇ 0.25; Cu ⁇ 0.04; Mn ⁇ 0.4; Cr 0.01 - ⁇ 0.1; Zn ⁇ 0.04; other elements ⁇ 0.05 each and ⁇ 0.15 in total, remains aluminum.
- a first object of the invention is a vacuum chamber element obtained by machining and surface treatment of a sheet of thickness at least equal to 10 mm of aluminum alloy composition, in% by weight, Si: 0 , 4 - 0.7; Mg: 0.4 - 1.0; the ratio in% by weight Mg / Si being less than 1.8; Ti: 0.01-0.15, Fe 0.08-0.25; Cu ⁇ 0.35; Mn ⁇ 0.4; Cr: ⁇ 0.25; Zn ⁇ 0.04; other elements ⁇ 0.05 each and ⁇ 0.15 in total, remains aluminum, characterized in that the grain size of said sheet is such that the mean linear intercept length ⁇ measured in the L / TC plane measured according to the ASTM El 12 standard, is at least equal to 350 ⁇ between surface and 1 ⁇ 2 thickness.
- a second object of the invention is a method of manufacturing a vacuum chamber element in which successively
- said rolling plate is homogenized
- said laminating plate is rolled at a temperature above 400 ° C to obtain a sheet of thickness at least equal to 10 mm,
- a solution treatment is carried out of said sheet, optionally preceded by a cold work-hardening operation, and quenched,
- an additional cold deformation of at least 3% and an annealing treatment at a temperature of at least 500 ° C are carried out, the annealing treatment being able to be carried out before or after the machining steps h or i and surface treatment,
- a surface treatment of the vacuum chamber element thus obtained preferably comprising anodization carried out at a temperature between 10 and 30 ° C., is carried out with a solution comprising 100 to 300 g / l of sulfuric acid and 10 to 30 g of sulfuric acid.
- g / 1 of oxalic acid and 5 to 30 g / l of at least one polyol said process comprising rolling steps and / or solution and / or additional cold deformation and annealing adapted to obtain a size of grain such as average linear intercept length ⁇ , measured in the L / TC plane according to the standard
- ASTM El 12 ie at least 350 ⁇ between surface and 1 ⁇ 2 thickness.
- Figure 1 shows the granular structure of product A obtained in Example 1 on L / TC sections after Barker attack.
- Figure 2 shows the geometry of the specimen used for the creep hot deformation tests.
- Figure 3 shows the granular structure of product F-1 (Figure 3A) and F-2 (Figure 3B) obtained in Example 2 on L / TC sections after Barker attack.
- FIG. 4 shows the granular structure of the products G and H obtained in Example 3 on L / TC sections after Barker etching, with a surface thickness of 1 ⁇ 4 and thickness 1 ⁇ 2.
- Figure 5 shows the stress profile in the thickness for the L direction of the products obtained in Example 3.
- the static mechanical characteristics in other words the ultimate tensile strength Rm, the conventional yield stress at 0.2% elongation Rp0.2 and the elongation at break A%, are determined by a tensile test according to ISO 6892-1, the sampling and the direction of the test being defined by EN 485-1.
- the hardness is measured according to EN ISO 6506.
- Grain sizes are measured according to ASTM Standard El 12. The average grain sizes are measured in the L / TC plane according to the intercept method of the standard (ASTM El 12-96 ⁇ 16.3). The average linear intercept length is measured in the longitudinal direction / / (°) and the transverse direction ((90 °). An average value in the plan
- L / TC £ (£ / (o ° £ (90 °) 1/2 )
- AI / £ /
- the term "grain size at the surface” is used to mean the grain size measured after machining, which makes it possible to remove 2 mm in the direction of the thickness.
- the breakdown voltage is measured according to EN ISO 2376: 2010.
- the present inventors have found that vacuum chamber elements having very advantageous properties in terms of resistance to high temperature creep deformation, while also having advantageous properties of corrosion resistance, uniformity of properties and machinability, are obtained for a specific aluminum alloy of the 6xxx series whose grain size is high and homogeneous in thickness relative to the known products according to the state of the art.
- a vacuum chamber element manufacturing method comprising steps for obtaining the grain size according to the invention has also been invented.
- composition of the aluminum alloy sheets for obtaining the vacuum chamber elements according to the invention is in% by weight, Si: 0.4 - 0.7; Mg: 0.4 - 1.0; the ratio in% by weight Mg / Si being less than 1.8; Ti: 0.01-0.15, Fe 0.08-0.25; Cu ⁇ 0.35; Mn ⁇ 0.4; Cr: ⁇ 0.25; Zn ⁇ 0.04; other elements ⁇ 0.05 each and ⁇ 0.15 in total, remains aluminum.
- Magnesium and silicon are the major additive elements in the alloy products according to the invention. Their content has been chosen with precision so as to achieve sufficient mechanical properties, including a tensile strength in the TL direction of at least 260 MPa and / or a yield strength in the TL direction of at least 200 MPa. and also a homogeneous granular structure in the thickness.
- the silicon content is between 0.4 and 0.7% by weight and preferably between 0.5% and 0.6% by weight.
- the magnesium content is between 0.4 and 1.0% by weight.
- the minimum magnesium content is 0.5% by weight.
- the maximum magnesium content is 0.7% by weight and preferably 0.6% by weight.
- the magnesium content is 0.4 to 0.7% by weight and preferably 0.5 to 0.6% by weight.
- the preferred contents of silicon and / or magnesium make it possible in particular to achieve, both at the surface and at mid-thickness, durations of appearance of hydrogen bubbles in the bubble test that are particularly remarkable for the products according to the invention.
- the ratio in%> by weight Mg / Si must remain less than 1.8 and preferably less than 1.5. The present inventors have indeed found that if this ratio is too high, resistance to deformation in creep at high temperature decreases. The present inventors believe that a Mg content too high in solid solution could affect resistance to high temperature creep deformation.
- the present inventors have found that, surprisingly, too little iron affects the resistance to high temperature creep deformation.
- the minimum iron content is 0.08% by weight and preferably 0.10% by weight. Too much iron can have a detrimental effect on the properties of the anodic oxide layer.
- the iron content is at most 0.25% by weight and preferably at most 0.20% by weight. In an advantageous embodiment of the invention, the iron content is from 0.10 to 0.20% by weight.
- the addition of too much copper content may have an adverse effect on resistance to high temperature creep deformation.
- the copper content is therefore less than 0.35% by weight.
- a high copper content can degrade the properties of the protective oxide layer and / or contaminate the products made in the vacuum chambers.
- the copper content is less than 0.05% by weight, preferably less than 0.02% by weight and preferably less than 0.01% by weight.
- the titanium content is less than 0.15% by weight.
- the addition of a small amount of titanium has a favorable effect on the granular structure and its homogeneity, so the titanium content is at least 0.01% by weight.
- the titanium content is 0.01 to 0.1% by weight and preferably 0.01 to 0.05% by weight.
- the titanium content is at least 0.02% by weight and preferably at least 0.03% by weight.
- the chromium content is less than 0.25% by weight.
- the addition of a small amount of chromium may have a favorable effect on the granular structure, so the chromium content is preferably at least 0.01% by weight.
- the chromium content is from 0.01 to 0.04% by weight and preferably from 0.01 to 0.03% by weight.
- the simultaneous addition of chromium and titanium is advantageous because it makes it possible in particular to improve the granular structure and in particular to reduce the anisotropy index of the grains.
- the manganese content is less than 0.4% by weight, preferably less than 0.04% by weight and preferably less than 0.02% by weight.
- the zinc content is less than 0.04% by weight, preferably less than 0.02% by weight and preferably less than 0.001% by weight.
- the aluminum alloy sheets according to the invention have a thickness of at least 10 mm.
- the aluminum alloy sheets according to the invention have a thickness of between 20 and 110 mm and preferably between 30 and 90 mm.
- the aluminum alloy sheets according to the invention have a thickness of at least 50 mm and preferably at least 60 mm.
- the sheets according to the invention have a grain size such that the average linear intercept length ⁇ measured in the L / TC plane according to the ASTM El 12 standard is at least equal to 350 ⁇ between surface and 1 ⁇ 2 thickness, and preferably at least equal to 400 ⁇ between surface and 1 ⁇ 2 thickness, which contributes to obtain resistance to high temperature creep deformation.
- the grain size is particularly homogeneous in the thickness, and the sheet is such that the variation in the thickness of the average linear interception length in the L / TC plane in the transverse direction, called °) according to ASTM El 12, is less than 30% and preferably less than 20%.
- the change in grain size is calculated by taking the difference between the maximum value and the minimum value at 1 ⁇ 2 thickness, 1 ⁇ 4 thickness and area and dividing by the mean values to 1 ⁇ 2 thickness, 1 ⁇ 4 thickness and area.
- the mean linear intercept length measured in the L / TC plane according to ASTM standard El 12 in the transverse direction ((90 °) is at least 200 ⁇ and preferably at least 230 ⁇ between surface and 1 ⁇ 2 thickness.
- the sheets according to the invention have a resistance to high temperature creep deformation.
- the strain creep under a stress of 5 MPa at 420 ° C is after 10 hours at most 0.40%> and preferably at most 0.27%>.
- the sheets according to the invention are suitable for machining.
- the stored elastic energy density Wtot the measurement of which is described in Example 1
- for the sheets according to the invention whose thickness is between 20 and 80 mm is advantageously less than 0.2 kJ / m 3.
- the vacuum chamber elements according to the invention are obtained by a process in which a. casting an aluminum alloy rolling plate of composition according to the invention,
- said rolling plate is homogenized
- said laminating plate is rolled at a temperature above 400 ° C to obtain a sheet of thickness at least equal to 10 mm,
- a solution treatment is carried out of said sheet, optionally preceded by a cold work-hardening operation, and quenched,
- an additional cold deformation of at least 3% and an annealing treatment at a temperature of at least 500 ° C are carried out, the annealing treatment being able to be carried out before or after the steps h or i of machining and surface treatment,
- a surface treatment of the vacuum chamber element thus obtained preferably comprising anodization carried out at a temperature between 10 and 30 ° C., is carried out with a solution comprising 100 to 300 g / l of sulfuric acid and 10 to 30 g of sulfuric acid. g / l of oxalic acid and 5 to 30 g / l of at least one polyol,
- the method comprising additional annealing and / or settling and / or cold deformation and annealing steps adapted to obtain a grain size such as mean linear intercept length ⁇ , measured in the L / TC plane according to the ASTM El 12 standard, ie at least 350 ⁇ between surface and 1 ⁇ 2 thickness.
- a grain size such as mean linear intercept length ⁇ , measured in the L / TC plane according to the ASTM El 12 standard, ie at least 350 ⁇ between surface and 1 ⁇ 2 thickness.
- Homogenization is advantageous, it is preferably carried out at a temperature between 540 ° C and 600 ° C. Preferably the homogenization time is at least 4 hours.
- the plate When homogenization is performed, the plate can be cooled after homogenization and then reheated before hot rolling or directly rolled after homogenization without intermediate cooling.
- the hot rolling conditions are important to obtain the desired microstructure, in particular to improve the corrosion resistance of the products.
- the rolling plate is maintained at a temperature above 400 ° C throughout the hot rolling.
- the temperature of the metal is at least 450 ° C during hot rolling.
- the sheets according to the invention are rolled to a thickness of at least 10 mm.
- a solution treatment is then carried out of the sheet optionally preceded by a cold work-hardening operation, and quenched.
- the quenching can be carried out in particular by spraying or immersion.
- the dissolution is preferably carried out at a temperature between 540 ° C and 600 ° C.
- Preferably the dissolution time is at least 15 min, the duration being adapted according to the thickness of the products.
- the sheet thus dissolved is then relieved by controlled traction with a permanent elongation of 1 to 5%.
- the tempering temperature is advantageously between 150 ° C. and 190 ° C.
- the duration of income is typically between 5h and 30h.
- an income is obtained at the peak making it possible to reach a maximum elasticity limit and / or a T651 state.
- an additional cold deformation of at least 3% and an annealing treatment at a temperature of at least 500 ° C. are carried out, the annealing treatment being carried out before or after the machining or surface treatment steps. .
- the rolling steps and / or dissolution and / or additional cold deformation and annealing are suitable.
- the rolling temperature is maintained at a temperature above 500 ° C and preferably above 525 ° C during all rolling steps.
- the natural logarithm of the Zener-Hollomon Z parameter defined by the equation (1), ln Z, is between 21 and 25 and preferably between 21.5 and 24.5 for the majority passes and preferably for all the passes made during hot rolling.
- e z e IQ (RT (i) where ⁇ is the average speed of deformation in the thickness expressed in s "1, Q is the energy 156 kJ activation / mole, R is the gas constant 8 , 31 JK 1 mol -1 , T is the rolling temperature expressed in Kelvin.
- the last rolling pass is advantageously such that L / H is at least 0.6 where H is the thickness at the mill inlet and L is the length of contact in the mill.
- the duration and / or the dissolution temperature are modified with respect to the duration and / or the dissolution temperature necessary to dissolve the alloying elements, so as to obtain a solution. grain enlargement.
- the time used is at least twice and / or the temperature is at least 10 ° C higher than the time and / or the dissolution temperature necessary to dissolve the alloying elements.
- the dissolution is preceded by a cold working operation by rolling or traction with a deformation of at least 4% and preferably at least 7%.
- an additional cold deformation of at least 3% is carried out after the tempering step and an annealing treatment at a temperature of at least 500 ° C., and preferably at least 525 ° C. C, the annealing treatment can be performed before or after the machining or surface treatment steps.
- the four embodiments can be combined to obtain the grain size according to the invention.
- a vacuum chamber element is obtained by machining and surface treatment of a sheet of thickness at least equal to 10 mm according to the invention.
- the surface treatment preferably comprises anodization treatment to obtain an anodic layer whose thickness is typically between 20 and 80 ⁇ .
- the surface treatment preferably comprises, before anodizing, degreasing and / or pickling with known products, typically alkaline products.
- the degreasing and / or pickling may comprise a neutralization operation especially in the case of alkaline pickling, typically with an acidic product such as nitric acid, and / or at least one rinsing step.
- the anodization is carried out using an acid solution. It is advantageous for the surface treatment to include, after anodization, a hydration (also called “sealing") of the anodic layer thus obtained.
- it is anodized at a temperature of between 10 and 30 ° C. with a solution comprising 100 to 300 g / l of sulfuric acid and 10 to 30 g / l of acid. oxalic acid and 5 to 30 g / l of at least one polyol and advantageously the product thus anodized is hydrated in deionized water at a temperature of at least 98 ° C preferably for a period of at least about 1 hour.
- the aqueous solution used for anodizing this advantageous surface treatment does not contain a titanium salt.
- the presence of at least one polyol in the anodizing solution also contributes to improving the corrosion resistance of the anode layers.
- Ethylene glycol, propylene glycol or preferably glycerol are advantageous polyols.
- the anodization is preferably carried out with a current density of between 1 and 5 A / dm 2 .
- the anodizing time is determined so as to reach the desired anodic layer thickness.
- a hydration step (also known as clogging) of the anodic layer.
- the hydration is carried out in deionized water at a temperature of at least 98 ° C preferably for a period of at least about 1 hour.
- the present inventors have observed that it is particularly advantageous to carry out the hydration after the anodization in two stages in deionized water, a first step lasting at least 10 minutes at a temperature of 20 to 20 minutes. 70 ° C and a second step of at least about 1 hour at a temperature of at least 98 ° C.
- a triazine-derived anti-dust additive such as Anodal-SHl® is added to the deionized water used for the second step of the hydration.
- Vacuum chamber elements treated with the advantageous surface treatment process and obtained from sheets having a thickness of between 20 and 80 mm easily reach, at mid-thickness, a duration of appearance of hydrogen bubbles in a 5% hydrochloric acid solution ("bubble test") of at least about 400 min and preferably at least 750 min and even at least about 900 min, at least for the portion corresponding to the surface of prison.
- the elements of vacuum chambers obtained from an alloy sheet according to the invention whose thickness is between 60 and 80 mm and with the advantageous surface treatment method can reach the surface of the sheet a duration the appearance of hydrogen bubbles in a 5% hydrochloric acid solution of at least 500 min and preferably at least 900 min at mid-thickness.
- vacuum chamber elements according to the invention in vacuum chambers is particularly advantageous because their properties are very homogeneous and moreover, especially for the anodized elements with the advantageous surface treatment method, the corrosion resistance is high which avoids the pollution of the products manufactured in the rooms such as, for example, microprocessors or slabs for flat screens.
- the plates were homogenized at a temperature of 560 ° C for 2 hours, hot rolled to a thickness of 16 mm at a temperature of at least 400 ° C.
- the sheets thus obtained were dissolved for 2 hours at a temperature of 575 ° C. (A, D, E), 545 ° C (C) or 570 ° C (B) adapted to their composition, quenched and triturated.
- the sheets obtained have a suitable income to reach a T651 state.
- the duration and temperature of the dissolution were intended to obtain a grain size such as the mean linear intercept length in the L / TC plane measured according to the ASTM standard.
- El 12, called £ is at least equal to 350 ⁇ between surface and 1 ⁇ 2 thickness.
- the micrograph obtained for sheet A, representative of all the sheets, is shown in FIG.
- Sheet A has undergone machining and surface treatment.
- the product is defatted, stripped with an alkaline solution, then neutralized with a nitric acid solution before undergoing anodization at a temperature of about 20 ° C in a sulpho-oxalic bath (Sulfuric acid 160 g / l + oxalic acid 20 g / l + 15 g / l glycerol).
- a hydration treatment of the anodic layer is carried out in two stages: 20 min at 50 ° C in deionized water and then about 80 min in deionized water to boiling in the presence of a derivative anti-dust additive Anodal-SH1® triazine.
- the anode layer obtained had a thickness of approximately 50 ⁇ .
- the anode layer obtained was characterized by the following tests.
- the breakdown voltage characterizes the voltage at which a first electrical current passes through the anode layer.
- the measurement method is described in EN ISO 2376: 2010. The value obtained was 2.6 kV.
- the "bubble test” is a corrosion test that makes it possible to characterize the quality of the anodic layer by measuring the duration of appearance of the first bubbles in a hydrochloric acid solution. A 20 mm diameter flat surface of the sample is contacted at room temperature with a 5% by weight solution of HCl. The characteristic time is the time from which a continuous flow of gas bubbles from at least one discrete point of the surface of the anodized aluminum is visible. The result was 450 minutes.
- alloy sheets of composition as indicated in Table 3 and thickness 280 mm were prepared by homogenization and hot rolling at a temperature above 400 ° C.
- the plates were homogenized at a temperature of 595 ° C for 12 hours.
- Plate G was hot rolled to a thickness of 64 mm at a temperature of at least 530 ° C and maintaining the Zener-Hollomon parameter for each rolling pass such that ln Z was between 22 and 24. 5.
- Plate H was hot-rolled to a thickness of 64 mm at a temperature of between 480 and 500 ° C, the Zener-Hollomon parameter being such that ln Z was greater than 26 for the majority of passes rolling.
- the sheets thus obtained were dissolved for 4 hours at a temperature of 535 ° C. and fractionated by 3%.
- the sheets obtained have a suitable income to reach a T651 state.
- the product G according to the invention has a larger grain size than the product H and also more homogeneous in the thickness.
- the residual stresses in the thickness were evaluated using the step-by-step machining method of rectangular bars taken in full thickness in the L and TL directions, described for example in the publication "Development of New Alloy for Distortion Free Machined Aluminum". Aircraft Components, "F.Heymes, B. Commet, B.Dubost, P.Lassince, P.Lequeu, GM.Raynaud, in I st International Non-Ferrous Processing & Technology Conference, 10-12 March 1997 - Adams's Mark Hotel, St. Louis, Missouri.
- This method applies mainly to plates whose length and width are significantly greater than the thickness and for which the residual stress state can be reasonably considered to be biaxial with its two principal components in the L and T directions ( ie no residual stress in the direction S) and such that the level of residual stresses varies only in the S direction.
- This method is based on the measurement of the deformation of two full-thickness rectangular bars which are cut in the plate along L and TL directions. These bars are machined down in the S direction step by step, and at each step the boom is measured, as well as the thickness of the machined bar.
- the width of the bar was 30 mm.
- the bar should be long enough to avoid any edge effects on the measurements.
- a length of 400 mm was used.
- Measurements are made after each machining pass. After each machining pass, the bar is removed from the vice, and a stabilization time is observed before the deformation measurement is performed, so as to obtain a uniform temperature in the bar after machining.
- the thickness h (i) of each bar and the arrow f (i) of each bar are collected.
- the elastic energy density stored in the Wtot bar can be calculated from the residual stress values using the following formulas:
- the measured total energy Wtot was 0.18 kJ / m 3 for sample G and 0.17 kJ / m 3 for sample H.
- the products have undergone machining and surface treatment.
- the product is defatted, stripped with an alkaline solution, then neutralized with a nitric acid solution before undergoing anodization at a temperature of about 20 ° C in a sulpho-oxalic bath (Sulfuric acid 160 g / l + oxalic acid 20 g / l + 15 g / l glycerol).
- a hydration treatment of the anodic layer is carried out in two stages: 20 min at 50 ° C in deionized water and then about 80 min in deionized water to boiling in the presence of a derivative anti-dust additive Anodal-SH1® triazine.
- the anode layer obtained had a thickness of approximately 50 ⁇ .
- the anode layers were characterized by the following tests.
- the breakdown voltage characterizes the voltage at which a first electrical current passes through the anode layer.
- the measurement method is described in EN ISO 2376: 2010. The values are given in absolute value after DC measurement.
- the "bubble test” is a corrosion test that makes it possible to characterize the quality of the anodic layer by measuring the duration of appearance of the first bubbles in a hydrochloric acid solution.
- a 20 mm diameter flat surface of the sample is contacted at room temperature with a 5% by weight solution of HCl.
- the characteristic time is the time from which a continuous flow of gas bubbles from at least one discrete point of the surface of the anodized aluminum is visible.
- the product according to the invention has excellent properties after surface treatment.
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Abstract
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Priority Applications (6)
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US16/492,085 US11248280B2 (en) | 2017-03-10 | 2018-03-01 | Aluminium alloy vacuum chamber elements stable at high temperature |
CN201880017403.3A CN110402296B (zh) | 2017-03-10 | 2018-03-01 | 高温稳定的铝合金真空室元件 |
KR1020197029492A KR102584052B1 (ko) | 2017-03-10 | 2018-03-01 | 고온 안정성의 알루미늄 합금 진공 챔버 요소 |
SG11201907957Y SG11201907957YA (en) | 2017-03-10 | 2018-03-01 | Aluminium alloy vacuum chamber elements stable at high temperature |
JP2019571109A JP2020510761A (ja) | 2017-03-10 | 2018-03-01 | 高温安定性のあるアルミニウム合金製真空チャンバ要素 |
EP18714563.6A EP3592875B1 (fr) | 2017-03-10 | 2018-03-01 | Elements de chambres a vide en alliage d'aluminium stables a haute temperature |
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FR1751981 | 2017-03-10 | ||
FR1751981A FR3063740B1 (fr) | 2017-03-10 | 2017-03-10 | Elements de chambres a vide en alliage d’aluminium stables a haute temperature |
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US (1) | US11248280B2 (fr) |
EP (1) | EP3592875B1 (fr) |
JP (1) | JP2020510761A (fr) |
KR (1) | KR102584052B1 (fr) |
CN (1) | CN110402296B (fr) |
FR (1) | FR3063740B1 (fr) |
SG (1) | SG11201907957YA (fr) |
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Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
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CN110129633A (zh) * | 2019-05-23 | 2019-08-16 | 江苏亨通电力特种导线有限公司 | 家具用铝合金铆钉线及其制备方法 |
WO2021064320A1 (fr) | 2019-10-04 | 2021-04-08 | Constellium Issoire | Toles de precision en alliage d'aluminium |
EP3938554B1 (fr) | 2019-03-13 | 2023-09-06 | Novelis, Inc. | Alliages d'aluminium durcissables par vieillissement et à formabilité élevée, feuille monolithique fabriquée à partir de ces derniers et produit en alliage d'aluminium plaqué la comprenant |
WO2023233090A1 (fr) | 2022-06-01 | 2023-12-07 | Constellium Valais Sa | Toles pour elements de chambres a vide en alliage d'aluminium |
Families Citing this family (4)
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CN111041294B9 (zh) * | 2019-12-31 | 2021-03-12 | 辽宁忠旺集团有限公司 | 具有高长期热稳定性的6系低合金成分及其制备方法 |
EP3922743A1 (fr) * | 2020-06-10 | 2021-12-15 | Aleris Rolled Products Germany GmbH | Procédé de fabrication de plaque d'aluminium pour chambres à vide |
CN113234972A (zh) * | 2021-04-30 | 2021-08-10 | 广东坚美铝型材厂(集团)有限公司 | 一种铝合金建筑模板及其制备方法 |
CN113684400A (zh) * | 2021-08-22 | 2021-11-23 | 山东华建铝业科技有限公司 | 一种高性能光伏铝合金边框及其生产工艺 |
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- 2018-03-01 CN CN201880017403.3A patent/CN110402296B/zh active Active
- 2018-03-01 WO PCT/FR2018/050481 patent/WO2018162823A1/fr active Application Filing
- 2018-03-01 JP JP2019571109A patent/JP2020510761A/ja active Pending
- 2018-03-01 SG SG11201907957Y patent/SG11201907957YA/en unknown
- 2018-03-01 EP EP18714563.6A patent/EP3592875B1/fr active Active
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Cited By (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP3938554B1 (fr) | 2019-03-13 | 2023-09-06 | Novelis, Inc. | Alliages d'aluminium durcissables par vieillissement et à formabilité élevée, feuille monolithique fabriquée à partir de ces derniers et produit en alliage d'aluminium plaqué la comprenant |
CN110129633A (zh) * | 2019-05-23 | 2019-08-16 | 江苏亨通电力特种导线有限公司 | 家具用铝合金铆钉线及其制备方法 |
CN110129633B (zh) * | 2019-05-23 | 2020-06-05 | 江苏亨通电力特种导线有限公司 | 家具用铝合金铆钉线及其制备方法 |
WO2021064320A1 (fr) | 2019-10-04 | 2021-04-08 | Constellium Issoire | Toles de precision en alliage d'aluminium |
FR3101641A1 (fr) | 2019-10-04 | 2021-04-09 | Constellium Issoire | Tôles de précision en alliage d’aluminium |
WO2023233090A1 (fr) | 2022-06-01 | 2023-12-07 | Constellium Valais Sa | Toles pour elements de chambres a vide en alliage d'aluminium |
FR3136242A1 (fr) | 2022-06-01 | 2023-12-08 | Constellium Valais | Tôles pour éléments de chambres à vide en alliage d’aluminium |
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EP3592875B1 (fr) | 2024-05-01 |
KR102584052B1 (ko) | 2023-09-27 |
CN110402296B (zh) | 2021-04-20 |
EP3592875C0 (fr) | 2024-05-01 |
EP3592875A1 (fr) | 2020-01-15 |
FR3063740B1 (fr) | 2019-03-15 |
JP2020510761A (ja) | 2020-04-09 |
FR3063740A1 (fr) | 2018-09-14 |
KR20190126851A (ko) | 2019-11-12 |
US11248280B2 (en) | 2022-02-15 |
TW201840864A (zh) | 2018-11-16 |
SG11201907957YA (en) | 2019-11-28 |
US20210130933A1 (en) | 2021-05-06 |
CN110402296A (zh) | 2019-11-01 |
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