IE54132B1 - Method of producing hot extruded products of high-strength alloys of type a1-zn-mg-cu with enhanced transverse tenacity - Google Patents

Method of producing hot extruded products of high-strength alloys of type a1-zn-mg-cu with enhanced transverse tenacity

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Publication number
IE54132B1
IE54132B1 IE2870/82A IE287082A IE54132B1 IE 54132 B1 IE54132 B1 IE 54132B1 IE 2870/82 A IE2870/82 A IE 2870/82A IE 287082 A IE287082 A IE 287082A IE 54132 B1 IE54132 B1 IE 54132B1
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product
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alloy
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Gerzat Metallurg
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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
    • C22F1/053—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 zinc as the next major constituent

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  • Chemical & Material Sciences (AREA)
  • Mechanical Engineering (AREA)
  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Physics & Mathematics (AREA)
  • Metallurgy (AREA)
  • Thermal Sciences (AREA)
  • Heat Treatment Of Steel (AREA)
  • Powder Metallurgy (AREA)
  • Heat Treatment Of Nonferrous Metals Or Alloys (AREA)
  • Extrusion Of Metal (AREA)
  • Manufacture And Refinement Of Metals (AREA)
  • Conductive Materials (AREA)

Abstract

1. A method of producing hot extruded products of the type Al-Zn-Mg-Cu, which, in the treated state, has improved transverse characteristics, characterised by casting an alloy of the following composition (% by weight) : Si =< 0.08 Cu 1.0 to 2.0 Mg 2.1 to 3.5 Zn 7.2 to 9.5 Cr 0.07 to 0.17 Mn 0.15 to 0.25 Zr 0.08 to 0.14 Ti =< 0.10 Others each =< 0.05 Others total =< 0.15 Balance = Al and iron homogenizing the cast product in the range of temperatures of from 460 degrees C to the initial melting temperature of the alloy, hot extruding the product at a temperature of the order of 400 degrees C, optionally hot drawing the hot extruded product, putting the product into solution in the range of temperatures of from 460 to 490 degrees C, quenching the product in cold water (omicron =< 40 degrees C), cold working with a level of deformation (S - s/s) =< 10%, and a tempering operation : type T6 : that is to say, from 6 to 50 hours at from 115 to 150 degrees C, or type T7 : that is to say, from 3 to 24 hours at from 100 to 120 degrees C + 8 to 20 hours at from 150 to 170 degrees C, the longest periods of time generally being associated with the lowest temperatures.

Description

METHOD OF PRODUCING HuT'IXTKUbED PRODUCTS OF HIGH-STRENGTH ALLOYS OF TYPE Al-Zn-Mg-Cu WITH ENHANCED TRANSVERSE TENACITY The present invention concerns a method of producing hot extruded products of high-strength aluminium alloy of type Al-Zn-Mg-Cu, which, in the treated state (type T6 or T7), have a high degree of ductility and tenacity, in particular in the transverse direction, and good resistance to stress corrosion.
High-strength hot extruded products are already known, which have high degrees of ductility and tenacity in the longitudinal direction (see for example the products described in French patent application No 2 457 908), However, for some uses, particularly in fields of use where the materials are subjected to very high stresses and must have a high level of reliability and safety in use (for example in the aeronautical industry, in armaments, etc...), the properties in the transverse direction are still unsatisfactory, in particular in the parts of the components which are relatively little worked.
The method comprises: - casting an alloy which is of the following composition (% by weight) Fe 0.10 Si £ 0.08 Cu 1.0 to 2.0 Mg 2.1 to 3.5 Zn 7.2 to 9.5 Cr 0.07 to 0.17 Mn 0.15 to 0.25 Zr 0,08 to 0.14 Ti < 0.10 others each << 0.05 others total 0.15 balance = Al - homogenizing the cast product in the temperature range of from 460°C to the initial melting temperature of the alloy - hot extruding the product at a temperature of the order of 400°C optionally hot drawing the hot extruded product at a temperature of the order of 380°C. putting the product into solution in the temperature range of from 460 to 480°C quenching the product in cold water (θ ί 40°C) optionally drawing the product in a cold condition with a degree of deformation s·) 10% - effecting a tempering operation: . type 16, that is to say, from 6 to 50 hours at from 115 to 150°C, or · type T7, that is to say, from 3 to 24 hours at from IOO to 12O°C + 8 to 20 hours at from 150 to 17O°C the longer periods of time generally being associated with the lower temperatures.
The optimum properties are achieved when each of the following conditions are preferably combined: 413 2 Analysis = Fe < 0.10 (% by weight) Si < 0.08 Cu : 1.35 to 1.85 Mg : 2.4 to 3.0 Zn : 7.6 to 8.9 Cr s 0.10 to 0.17 Mn : 0.15 to 0.25 Zr s 0.08 to 0.14 Ti < 0,10 Others each ~ 0,05 Others Total <0.15 Balance Al Homogenization at about 47O°C - 5°C Solution treatment at from 465 to 480°C Cold working (S ~ ) of from 1,5 to 5% Tempering : type T6 ί 25 to 35 hours at from 115 to I3O°C, or type T7 : 5 to 10 hours at from 100 to 11O°C + 8 to 12 hours at from 155 to 165°C It has been noted that the proportions of main alloy 20 elements must be sufficient to produce the required mechanical characteristics but must be limited in an upward direction in order not to induce excessive fragility. Transverse ductility is also highly influenced by the proportions of Fe and Si which should preferably be as low as possible, within the following limits i Fe 4 0.05% Si £ 0.05% Fe + Si 0.06% The following examples illustrate the properties obtained 30 in the case of a hollow extruded member and a n extruded * bar; Figure 1 shows details of the operation of taking samples, and Figure 2 shows the design of the sample for determining the factor K (see the appendix) - dimensions in nun.
EXAMPLE 1 Two alloys A and B were cast, the compositions of the alloys being as set out below, with the alloy A which is not in accordance with the invention forming the reference: (% by weight) A B Fe 0.14 0.05 Si 0.06 0.04 Cu 1.63 1.60 Zn 8.13 8.00 Mg 2.69 2.46 Mn 0.18 0.20 Cr 0.13 0.12 Zr 0.11 0.13 Ti < 0.05 < 0.05 The alloy A which is semi-continuously cast in the form of billets with a diameter of 170 mm was subjected to a homogenization treatment for 24 hours at a temperature of 460°C, and hot extruded by reverse extrusion at a temperature of 400°C ί 10°C, in the form of case members measuring φ 107 X 141 mm. The case members were drawn in the hot condition at a temperature of 380°C - 20°C, to the following dimensions: φ 105.5 X 132 mm, externally machined by turning to a diameter of 127.2 mm, cleaned, subjected to solution treatment at a temperature of 46O°C, quenched in cold water, subjected to cold drawing on fresh quenching with a degree of cold working ~ s) of 4% and tempering for 30 hours at a temperature of 120°C.
Alloy B m accordance with the invention was divided into four batches: Bl, B2, B3 and B4; " batch Bl was transformed in an identical manner to batch A, except for the degree of cold working (*» ~ s) which was 10% instead of 4%; - batch B2 was transformed in an identical manner to batch A} - batch B3 was transformed in an identical manner to batch B2, except that the homogenization treatment was performed at a temperature of 47O°C (instead of 460°C) and the solution treatment was performed at a temperature of 47O°C (instead of 460°C); batch B3 IO therefore corresponds to the preferred range of the invention; and - batch B4 was transformed in an identical fashion to batch B2, except as regards the final tempering operation carried out: 6 hours at 1O5°C + 10 hours at 150°C, 155°C, 160°C and 165°C (batches B41, B42, B43 and B44 respectively) or at a temperature of 120°C for 30 hours (batch B40).
The following were machined from the resulting case members (see Figure l)s - smooth tensile stress test pieces (l) which axe taken either from the body of the case member, distinguishing between the longitudinal direction (L) and the transverse direction (tangential direction T), or from the bottom of the case member in the transverse direction (T) (tangential direction). Through the tensile stress test, the test pieces were used to determine conventional mechanical characteristics, namely . elastic limit RO.2 . 'tensile stress Rm . elongation to rupture A % as measured over an initial useful length equal to 5'. 65 V So, So being the section of the test piece before tensile stress; - notched tensile stress test pieces (2) with a coefficient of concentration of stress Kj. = 6.5 (radius at notch bottom 0.025 mm), which are taken in the longitudinal direction of the body portion of the case member. The test pieces were broken by tensile stress, which permitted their breaking stress Re to be determined. The ratio Re/R0.2 of the breaking stress on a notched test piece to the elastic limit on a smooth test piece was taken as an evaluation criterion;.
- Charpy V type notched impact test pieces (3) (45° V-shaped notch, 2 mm in depth, with a radius at the notch bottom of 0.25 mm). The test pieces were taken in the longitudinal direction of the body portion of the case members, so that the rupture crack is propagated in the direction of the thickness of the body portion of the case member (standardized direction L-R). They were used for determining the following characteristics: Enc'(rupture energy on non-precracked test piece) and Eco (rupture energy on a test piece which was pre-cracked by fatigue on a Physmet apparatus); - test pieces (4) for measuring the tenacity factor K; the conditions of determining the factor K are set forth in the appendix; - test pieces for corrosion tests in the form of rings C taken from the body portion, 40’mm in width. The test pieces were tested in respect of stress corrosion in accordance with standard AFNOR A 05-301.
The results (mean values) are set out in Table I in the appendix.
It will be observed in respect of the members Al, Bl, B2 and B3, which are treated in the T6 mode, that the batches Bl, B2 and B3 in accordance with the invention have degrees of §413A elongation to rupture, in the transverse direction of the part of the bottom which is relatively slightly worked, that are markedly higher than those of the reference batch Al. Moreover, batch B2, which was subjected to a cold working operation after quenching and before tempering, in the preferred range of the invention (^1.5% and ^5%) has a set of tensile stress characteristics, at a higher level of performance than batch Bl in which the degree of cold working was 10%.
In addition, batch B3, in respect of which the conditions of homogenization, solution treatment, cold working between quenching and tempering, are in the preferred range of the invention, appears to provide a particularly high level of performance, in particular as regards elongation to rupture in the transverse direction of the bottom of the case member, being more than four times the values of the reference batch A.
Finally, batches B4x show that, for a treatment of type 17 with two stages, it is possible for the alloys in accordance with the invention to have a particularly high level of resista.nce to stress corrosion.
EXAMPLE 2 Three alloys C, D and E of the following composition were cast semi-continuously, in the form of 200 mm diameter billets: (% by weight) C D E Fe 0.16 0.09 0.02 Si 0.10 0.05 0.02 Cu 1.45 1.45 1.45 Mg 2.65 2.65 2.65 Zn 8.10 8.10 8.10 Mn 0.22 0.21 0.22 Cr 0.15 0.10 0.16 Zx 0.11 0.12 0.11 Ti 0.05 0.05 0.05 alloy C, which is not in accordance with the invention, constituting the reference.
Each of the alloys was homogenized for a period of 24 hours at 47S°C, a surface layer was removed to give a diameter of 170 mm, and the alloys were converted by reverse hot extrusion at a temperature of 350 to 400°C, in the form of a 50 mm diameter bar. The bars were put into solution for 1 hour at 478°C, quenched in cold water and tempered for 24 hours at 12O°C.
The following test pieces were taken from the bars, for test purposes: - smooth tensile stress test pieces, in the longitudinal and transverse directions, for measuring the characteristics RO.2, Rm and A % (over 5.65V So); - notched tensile stress pieces with a coefficient of concentration of stress equal to 8, in the transverse direction, for measuring Re and determining the ratio Re/RO.2; - tenacity test test pieces (format: 30 X 31.25, thickness: 12.5 mm) in the directions L-R and C-R (ASTM designation).
The test conditions, corresponding to the specification of ASTM E399, permitted the stress concentration factor Kjc to be determined.
The results (mean values) are set out in Table 2 below.
TABLE 2 R0.2 (MPa) Rm (MPa) A (%) * Direction Alloy C Alloy D Alloy E L T L T L T 690 545 715 605 5 4.9 690 540 720 610 5.5 6.5 685 540 705 610 5.5 6.6 Re/RO.2 T 0.90 1.20 1.30 10KIc L-R C-R 32 22 35 24 38 29 fK!cY W \R0.2/ L 0.215 0.255 0.310 T 0.163 0.198 0.290 * L : long T s transverse C : circumferential R : radial Note should be taken in particular of the improvement in 15 the properties in the transverse direction, regarding more particularly plasticity (A %) and tenacity (Re/R0.2 and Kjc) in the case of alloys D and E in accordance with the invention, alloy E corresponding to the preferred range of composition of the invention, and having the best performance in that respect.
It should be noted that the value of the ratio (^—_) which is K0« 2 representative of the critical length of a crack giving rise to catastrophic rupture of the corresponding member is almost equal in the transverse and longitudinal directions, in regard to the last-mentioned alloy. 413 3 APPENDIX MEASURING THE TENACITY FACTOR K The test test piece is shown in Figure 2.
The dimensions of the test piece are as follows: - thickness : B = 8mm - width : W = 8mm - length : 55mm - machined notch : a = 2mm radius at notch bottom O.O8mm.
A fatigue crack is initiated in the above-defined test piece, which is taken in the body portion in the direction L-R, under the conditions set forth in standard ASTM E399 (0.45 -c a/w < 0.55, propagation in respect of fatigue of at least 1.3mm, load less than 60% of the Pq).
The fatigue-cracked test piece is then subjected to a test involving slow bending at three points. During the test, a record is made of the curve: force as a function of the speed of movement of the paper of the recorder (constant speed).
The factor K was calculated in accordance with the formula set forth in standard ASTM E399 (Bend Specimen) which is as follows: "' · I' I (in MPa ψη) wherein; P ; maximum load measured on the graph in newtons S : distance between supports in metres W : width of the test piece in metres B : thickness of the test piece in metres a : length of the crack in metres Π Remark: Measuring the length a of the crack.
The test piece, after breaking, is projected onto a frosted glass screen by means of a profiloscope (g = 20), The part of the fracture which corresponds to the 5 initial crack produced by fatigue is then traced off onto transparent paper. Measurements are then taken in respect of the lengths of the cracks at a quarter, a half and three quarters of the thickness of the test piece.
The value of a which is used in the formula is the IO mean value of the three measurements. 413 2 (d) no cracking under a load of 330 MPa TJ ¢1 1-10 DO to CO CO CO A £ A £ £ .HjJNHO Β3 Β2 CD Η» is Case CT σ σ σ u 0 σ 0 σ' 0 σ 0 σ 0 0 0 <+ 0 <+ 0 Ul α 0. 1+ 0. r+ a. P· 0 ν; 0 0 0 'a <+ 3 Ξ 3 3 W· 3 σ Η· Η Η Γ H r ι η r H r H r ι h r κ (0 » Λ 0 <+ 0 3 Ui In Ui Ui Ot Ui Ot O' Ui Vl 0> Ui Ui Ui O' O' M a Ol Ό H CD Ο ω Οι Ot to A 10 00 ω ω X Ο Ό 03 03Ο03 o Ui ο ο o o o o Ui Ui o ή · Ρ Μ Ul Ol Ot Ol Ot Ol ot σ Οΐ οι σ Oi Oi Ot σ ο cd ο μ ω oi y 0\ Οι Η Vi Vl o ω H 0i Ul ω ω H H Ul o ο ο Ui Ui Ui Ui o O Ul Ρ μι μ. μι |_ι Η Η 00 W ω Ui 10 10 0i 10 ID oo ω 58 > • · · · · • · • • · • • • • · θ' Ί Ό * Ο ω Ο 01 Oi 00 H to ω o O Ul H* Φ • • \ ω ω Λ Ui Ui ο Μ (0 w ^»Ρ1 • • C, 3 Ui CD *~Ό ω to H • • «**· tn 10 ω C, 0 ω ω *-*0 X ω w s Ui Ό < Ώ • •M 1 Ρ X A H 3 1 o o »1 • • *3 οχ ω ro • ι to H w| Ui A ω C+ V Η H V H Κ Φ ω (η ω ω ω w μ Α .U A * Ul Ul Ul Α 00 ο o o * η Ui.lu.Ui.U.U. 0 ΜκΜ'Μ'Μ'Μ', Μ* Z·» κ &ο.Β.η σ Ρ p κ •s·»» **·«*«*'*»*<’·»·· *W«* ·»✓ 0 ω Η· 0 3 TABLE 1

Claims (10)

1. A method of producing hot extruded products of the type Al-Zn-Mg-Cu, which, in the treated state, has improved transverse characteristics, comprising casting an alloy of the following composition (.% by weight): Fe^ 0.10 5 Si 4ΓΟ.Ο8 Cu 1.0 to 2.0 Mg 2.1 to 3.5 Zn 7.2 to 9.5 Cr 0.07 to 0.17 10 Mn 0.15 to 0.25 Zr 0.08 to 0.14 Ti ^0.10 Others each 0.05 Others total ^0.15 15 Balance = Al homogenizing the cast product in the range of temperature of from 460°C to the initial melting temperature of the alloy, hot extruding the product at a temperature of the order of 400θ0, optionally hot drawing the hot extruded product, putting the product into solution in the range of 20 temperatures of from 460 to 480°C, quenching the product in cold water (S^40°C), cold working with a level of deformation ~ s ) ^10%, and a tempering operation: type Tg: that is to say, from 6 to 50 hours at from 115 to 150°C, or 25 type T?: that is to say, from 3 to 24 hours at from 100 to 120°C + 8 to 20 hours at from 150 to 170°C, the longest periods of time generally being associated with the lowest temperatures.
2. A method according to claim 1 wherein the alloy is of the following 30 preferred composition (% hy weight): Fe <0.10 Si <0.08 Cu 1.35 to 1.85 Mg 2.4 to 1 t.O Zn 7.6 to ε 1.9 Cr 0.10 to 0.17 Mn 0.15 to 0.25 Zr 0.08 to 0.14 Ti < 0.10 10 Others each < 0.05 Others total <0.15 Balance = Al
3. A method according to claim 1 or claim 2 wherein the proportions of Fe and Si are limited to (% by weight): Fe <0.05 15 Si < 0.05 Fe + Si < 0.06
4. A method according to one of claims 1 to 3 wherein the homogenization operation is carried out from 465 to 475°C.
5. A method according to one of claims 1 to 4 wherein the solution 20 treatment is performed at from 465 to 480°C.
6. A method according to one of claims 1 to 5 wherein the degree of cold working (--· 5 ·-·) is from 1.5 to 5%.
7. A method according to one of claims 1 to 6 wherein tempering is effected in the range of temperatures of from 115 to 130°C for a period 25 of from 25 to 35 hours.
8. A method according to one of claims 1 to 6 wherein the tempering operation comprises a residence period of from 5 to 10 hours at from 100 to 110°C and a residence period of from 8 to 12 hours at from 155 to 165°C.
9. A method of producing hot extruded products substantially as described herein with reference to the Examples.
10. Hot extruded products whenever prepared by a method according to any preceding claim.
IE2870/82A 1981-12-03 1982-12-02 Method of producing hot extruded products of high-strength alloys of type a1-zn-mg-cu with enhanced transverse tenacity IE54132B1 (en)

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DE (1) DE3267187D1 (en)
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FR (1) FR2517702B1 (en)
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US8524014B2 (en) 2000-12-21 2013-09-03 Alcoa Inc. Aluminum alloy products having improved property combinations and method for artificially aging same

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EP0081441B1 (en) 1985-10-30
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CA1206354A (en) 1986-06-24
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FR2517702B1 (en) 1985-11-15
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