Construction and Verification of the Constitutive Model of Pure Copper Deformation at Elevated Temperatures
The deformation behavior of pure copper was studied in hot compression tests in the temperature range of 773–1173 K and strain rate interval of 0.001–1.0 s⁻¹, the corresponding flow stress curves were plotted. The new method to calculate critical and saturation stresses was devised, quantitative ana...
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Інститут проблем міцності ім. Г.С. Писаренко НАН України
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irk-123456789-1883102023-02-23T01:27:22Z Construction and Verification of the Constitutive Model of Pure Copper Deformation at Elevated Temperatures Huang, S.H. Wu, Y. Zhao, Z.D. Xia, X.S. Научно-технический раздел The deformation behavior of pure copper was studied in hot compression tests in the temperature range of 773–1173 K and strain rate interval of 0.001–1.0 s⁻¹, the corresponding flow stress curves were plotted. The new method to calculate critical and saturation stresses was devised, quantitative analysis of strain hardening and dynamic softening was presented, a three-stage constitutive model was constructed to predict the flow stress of pure copper. As predicted and measured flow stress comparison indicate, the physical constitutive model can accurately characterize hot deformation of pure copper. With dynamic recovery and/or recrystallization. Numerical simulation of an upsetting process is carried out by implementing the constitutive model into commercial software. This model can be put to practical use and be quite promising for improving efficiency of a hot forging process for pure copper components. Изучено деформационное поведение чистой меди при испытании горячих проб на сжатие в диапазоне температур 773 1173 К и скорости деформации 0.001–1.0 с⁻¹, построены соответствующие кривые напряжения пластического течения. Разработан новый метод расчета критического напряжения и напряжения насыщения, представлен количественный анализ деформационного упрочнения и динамического разупрочнения, построена трехступенчатая определяющая модель прогнозирования напряжения пластического течения чистой меди. Как показывает сравнение прогнозируемого и измеренного напряжений пластического течения, с помощью такой модели можно точно описать горячее деформирование чистой меди при динамическом возврате и/или рекристаллизации. Выполнено численное моделирование процесса высадки путем реализации данной модели в рамках коммерческого программного обеспечения. Модель весьма перспективна и может использоваться для повышения эффективности процесса горячей ковки деталей из чистой меди. Вивчено деформаційне поведінку чистої міді при випробуванні гарячих проб на стиск в діапазоні температур 773-1173 К і швидкості деформації 0.001–1.0 с⁻¹, побудовані відповідні криві напружень пластичної течії. Розроблено новий метод розрахунку критичної напруги і напруги насичення, представлений кількісний аналіз деформаційного зміцнення і динамічного знеміцнення, побудована триступенева визначає модель прогнозування напружень пластичної течії чистої міді. Як показує порівняння прогнозованого і виміряного напружень пластичної течії, за допомогою такої моделі можна точно описати гаряче деформування чистої міді при динамічному поверненні і / або рекристалізації. Виконано чисельне моделювання процесу висадки шляхом реалізації даної моделі в рамках комерційного програмного забезпечення. Модель вельми перспективна і може використовуватися для підвищення ефективності процесу гарячого кування деталей з чистої міді. 2019 Article Construction and Verification of the Constitutive Model of Pure Copper Deformation at Elevated Temperatures / S.H. Huang, Y. Wu, Z.D. Zhao, X.S. Xia // Проблеми міцності. — 2019. — № 1. — С. 127-136. — Бібліогр.: 16 назв. — англ. 0556-171X http://dspace.nbuv.gov.ua/handle/123456789/188310 539.4 en Проблемы прочности Інститут проблем міцності ім. Г.С. Писаренко НАН України |
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Научно-технический раздел Научно-технический раздел Huang, S.H. Wu, Y. Zhao, Z.D. Xia, X.S. Construction and Verification of the Constitutive Model of Pure Copper Deformation at Elevated Temperatures Проблемы прочности |
| description |
The deformation behavior of pure copper was studied in hot compression tests in the temperature range of 773–1173 K and strain rate interval of 0.001–1.0 s⁻¹, the corresponding flow stress curves were plotted. The new method to calculate critical and saturation stresses was devised, quantitative analysis of strain hardening and dynamic softening was presented, a three-stage constitutive model was constructed to predict the flow stress of pure copper. As predicted and measured flow stress comparison indicate, the physical constitutive model can accurately characterize hot deformation of pure copper. With dynamic recovery and/or recrystallization. Numerical simulation of an upsetting process is carried out by implementing the constitutive model into commercial software. This model can be put to practical use and be quite promising for improving efficiency of a hot forging process for pure copper components. |
| format |
Article |
| author |
Huang, S.H. Wu, Y. Zhao, Z.D. Xia, X.S. |
| author_facet |
Huang, S.H. Wu, Y. Zhao, Z.D. Xia, X.S. |
| author_sort |
Huang, S.H. |
| title |
Construction and Verification of the Constitutive Model of Pure Copper Deformation at Elevated Temperatures |
| title_short |
Construction and Verification of the Constitutive Model of Pure Copper Deformation at Elevated Temperatures |
| title_full |
Construction and Verification of the Constitutive Model of Pure Copper Deformation at Elevated Temperatures |
| title_fullStr |
Construction and Verification of the Constitutive Model of Pure Copper Deformation at Elevated Temperatures |
| title_full_unstemmed |
Construction and Verification of the Constitutive Model of Pure Copper Deformation at Elevated Temperatures |
| title_sort |
construction and verification of the constitutive model of pure copper deformation at elevated temperatures |
| publisher |
Інститут проблем міцності ім. Г.С. Писаренко НАН України |
| publishDate |
2019 |
| topic_facet |
Научно-технический раздел |
| url |
http://dspace.nbuv.gov.ua/handle/123456789/188310 |
| citation_txt |
Construction and Verification of the Constitutive Model of Pure Copper Deformation at Elevated Temperatures / S.H. Huang, Y. Wu, Z.D. Zhao, X.S. Xia // Проблеми міцності. — 2019. — № 1. — С. 127-136. — Бібліогр.: 16 назв. — англ. |
| series |
Проблемы прочности |
| work_keys_str_mv |
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| first_indexed |
2025-07-16T10:18:55Z |
| last_indexed |
2025-07-16T10:18:55Z |
| _version_ |
1837798403541565440 |
| fulltext |
UDC 539.4
Construction and Verification of the Constitutive Model of Pure Copper
Deformation at Elevated Temperatures
S. H. Huang,
a,b,1
Y. Wu,
a
Z. D. Zhao,
a,b
and X. S. Xia
a
a Southwest Technology and Engineering Research Institute, Chongqing, China
b Precision Forming Integrated Manufacturing Technology of Collaborative Innovation Center,
Chongqing, China
1 hsh82@163.com
The deformation behavior of pure copper was studied in hot compression tests in the temperature
range of 773–1173 K and strain rate interval of 0.001–1.0 s 1� , the corresponding flow stress curves
were plotted. The new method to calculate critical and saturation stresses was devised, quantitative
analysis of strain hardening and dynamic softening was presented, a three-stage constitutive model
was constructed to predict the flow stress of pure copper. As predicted and measured flow stress
comparison indicate, the physical constitutive model can accurately characterize hot deformation of
pure copper. With dynamic recovery and/or recrystallization. Numerical simulation of an upsetting
process is carried out by implementing the constitutive model into commercial software. This model
can be put to practical use and be quite promising for improving efficiency of a hot forging process
for pure copper components.
Keywords: pure copper, constitutive model, flow stress, numerical simulation, dynamic
recrystallization.
N o t a t i o n
DRV – dynamic recovery
DRX – dynamic recrystallization
X drx – DRX fraction
� �, – stress and strain, respectively
�wh – work hardening stress
� rec – dynamic recovery stress
� reci – ith process stress
� drx – dynamic recrystallization stress
� sat – saturated stress
� �0 0, – initial yield stress and strain
� �c c, – critical stress and strain
� �p p, – peak stress and strain
� �ss ss, – steady state stress and strain
� i – ith process strain
r – parameter of DRV
n k, – Avrami’s power and constant
T – temperature
Tr – reference temperature
Tm – melting point of the material
© S. H. HUANG, Y. WU, Z. D. ZHAO, X. S. XIA, 2019
ISSN 0556-171X. Ïðîáëåìè ì³öíîñò³, 2019, ¹ 1 127
� 0r – yield stress at reference temperature and particular strain rate
� – strain hardening rate
�� c – primary partial derivative value of � and � corresponding to critical
stress � c
��� � �T �
– secondary partial derivative function of strain hardening rate vs stress
�� – strain rate
��r – reference strain rate
B C q, , – constants of Johnson–Cook model
a b ci j k, , – parameters (i� 0, 1, ..., 9; j� 0, 1, ..., 5; k� 0, 1, ..., 3)
Introduction. Pure copper, with its excellent combination of such properties as good
plasticity and high density, is widely applied to the manufacturing of high-precision and
complex products [1, 2]. To achieve the process optimization and obtain products with
precise geometrical shape and fine and uniform crystalline grains, it is required to study the
high-temperature deformation behavior of pure copper. Thermal simulation compression
test is often used to simulate condition of forging technology, and a constitutive model of
the material is established to reveal the work hardening and softening behaviors and
provide a numerical simulation of the products’ processing [3–5].
It is well known that the main softening mechanisms of alloys under hot deformation
are dynamic recovery (DRV) and dynamic recrystallization (DRX) [6–13]. The flow stress
functions of DRV and DRX are given by Eqs. (1) and (2), respectively:
� � � � � �rec sat sat r� � � � �{ ( )exp[ ( )]} ,/2 2
0
2
0
1 2 � � �0 c , (1)
� � � �
� �
�drx rec sat ss
c
p
n
k� � � � �
�
�
�
�
�
�
�
�
�
�
�
�
�
�
�
( ) exp1
�
�
�
��
�
�
�
��
, � � �c ss . (2)
If the DRX does not initiate, as shown in Fig. 1a, the so-called saturation stress (if
DRV is the only softening mechanism) can be measured directly from the flow curves. If
the flow curve displays an apparent softening regime due to DRX, the saturation stress does
not practically exist, but nevertheless can be extrapolated from the work-hardening rate
curve under the assumption that only DRV occurred (Fig. 1b). The softening caused by
DRX can be measured subsequently by using this hypothetical saturation stress and the
practical flow curve.
S. H. Huang, Y. Wu, Z. D. Zhao, and X. S. Xia
128 ISSN 0556-171X. Ïðîáëåìè ì³öíîñò³, 2019, ¹ 1
a b
Fig. 1. (a) Schematic description of the flow behavior at high temperature; (b) corresponding flow
stress dependence of the strain hardening rate.
At present, the following two methods based on Eq. (1) are mainly used to determine
the value of � sat [6–13]. In the first method, using Eqs. (3) and (4), the linear regression of
�� �rec rec� 2 curve is performed to get m and r values:
�� � �rec sat rec
r
� �
2
2 2( ), � � �0 c , (3)
m
rrec
rec
� ��
� ��
� �
( )
( )
,
2 2
(4)
With �� rec � 0, the stress corresponding to �� �rec rec� 2 curve is the squared saturation
stress � sat
2 .
The second method adopts Eq. (5) to yield the primary partial derivative value �� c of
� and � corresponding to critical stress (� c ) point. Here the � �� curve extends outward
to �� 0 along the tangent line at the critical stress (� c ) point, and Eq. (6) is used to obtain
the saturation stress( ):� sat
� ��
��
�� �
c
c
, (5)
� � � �sat c c c� � � . (6)
Because of a relatively large fluctuation of the measured stress–strain curve data, there
is also a comparatively large scatter in the values of strain hardening rate � obtained from
calculation of � �� �. There is no obvious pattern in the � �� data curve, as in Fig. 1b, but
a relatively large scatter in data exists [4, 5, 12, 13]. It is very difficult to calculate and
determine the critical stress � c via the above methods, which complicates further
determination of such parameters as the saturation stress � sat and DRV parameter r.
Eventually, it deteriorates the accuracy of fitting calculation of Eqs. (1) and (2). In this
study, a new method for estimating the critical and saturated stresses is proposed and
verified.
1. Experimental Procedures. Before the experiment, a pure copper bar was provided
by the Luoyang Copper Co., Ltd. (China), which was annealed at 693 K for 2 h, and then
scalped to diameter of 8 mm and height of 12 mm from the same area, with grooves on
both sides filled with machine oil mingled with graphite powder as lubrication. Then,
isothermal compression tests were performed on a Gleeble 1500 thermal-mechanical
simulator. The specimens were resistance heated at a heating rate of 1 K/s and held at a
certain temperature for 180 s to ensure a uniform starting temperature and decrease the
material anisotropy. All specimens were compressed to a true strain of 0.9163 (height
reduction of 60%) at the temperatures of 773, 873, 973, 1023, 1073, 1123, and 1173 K, and
the strain rates of 0.001, 0.01, 0.1, and 1 s�1. The true compressive stress–strain curves at
seven temperatures and four strain rates are shown in Fig. 2.
2. Principles of Physically-Based Constitutive Model. Following methods were
primarily used to establish constitutive model of pure copper that considers the work
hardening and softening effect.
(1) The stress–strain relationship under isothermal constant strain rate was established.
To be unified with the function expression in Eq. (1), the function relationship in Eq. (7)
was used to conduct fitting calculation of the practically-measured stress–strain data,
thereby determining relative parameters of f ( )� function. Where, g ( )� is the function
related to strain �. The expressions of primary partial derivative function �f ( ),� secondary
Construction and Verification of the Constitutive Model ...
ISSN 0556-171X. Ïðîáëåìè ì³öíîñò³, 2019, ¹ 1 129
partial derivative function ��f ( ),� and third partial derivative function ���f ( )� corresponding
to f ( )� are shown in Eqs. (8), (9), and (10):
ln ( ) ln{ ( )exp[ ( )]},, �� � � � � ��T sat satf g� � � �
1
2
2 2
0
2 � �0 09163 . , (7)
� �
�
� �f g f g
sat
( )
( )
exp[ ( ) ( )] ( ),�
� �
� � �0
2 2
2
2 (8)
�� �
�
� �� � � �f g f g g g
sat
( )
( )
exp[ ( ) ( )]{ ( ) ( )[�
� �
� � � �0
2 2
2
2 ( ) ( )]},� �� �2 f (9)
��� �
�
�
���
� ��
f g f
g
g
sat
( )
( )
exp[ ( ) ( )]
( )
( )
�
� �
� �
�
�
0
2 2
2
2
2 [ ( ) ( )]
( )[ ( ) ( )]
( )[ ( )
� � �
� � �� � ��
� � � �
g f
g g f
g g
� �
� � �
� �
2
2
2 �
�
�
�
�
�
�
�
�
�
�
�
�
�
�f ( )]
.
� 2
(10)
The function of strain hardening rate and strain can be derived in the following
form:
130 ISSN 0556-171X. Ïðîáëåìè ì³öíîñò³, 2019, ¹ 1
S. H. Huang, Y. Wu, Z. D. Zhao, and X. S. Xia
Fig. 2. True stress–strain curves of pure copper at different strain rates: 0.001 (a), 0.01 (b), 0.1 (c),
and 1 s�1 (d).
a b
c d
�
��
��
�
� �
��
� ��T f, �
ln
( ),� � � � � �0 09163 . . (11)
Established curve of strain hardening rate and stress, or curve of strain hardening rate
and strain, when � �T , � value was equal to 0 for the first time, peak stress � p or peak
strain � p was determined, and when � �T , � was equal to 0 for the second time, steady state
stress � ss or steady state strain �ss was determined.
(2) Based on Eq. (11) it was deduced to obtain the secondary partial derivative
function of strain hardening rate vs stress, as shown in Eq. (12):
�� � �
�� �
��
�
�
���
�
�
� �
��
�
�
�
�
�T
f
f
f
f
f
, �
( )
{ ( )}
{ ( )}
( )
(2
2
2
2 �
� �
)
exp( ( )) ( )
,
f f �
� �0 09163 . . (12)
Under condition of � � �0 p , the strain corresponding to the routine calculation
objective function �� �� �T , � ,0 i.e., critical strain �c , was derived. Thus, the critical stress � c
was converted from Eq. (7).
(3) Under the condition of � � �0 i c , � �p sat , r 0, yield stress � 0, yield strain
�0 , critical stress � c , and critical strain �c were substituted into Eqs. (3)–(6) to construct
the routine calculation objective function � � � � �reci sat sat ig� � �{ ( )exp[ ( )]} /2 2
0
2 1 2 and
� � � �sat c c c� � � , then, g ri i( ) ( ),� � ��� � 0 where � i denotes the ith process strain,
� reci represents ith process stress, calculation was conducted to obtain saturation stress
� sat , parameter r, to get � rec curve data under isothermal constant strain rate. By
repeating the above procedure, � rec curve data could be obtained under different
temperatures and strain rates.
(4) After � rec , � sat , � ss , �c , and � p data were obtained for different temperatures
and strain rates, the measured values � drx and their corresponding � data were substituted
into Eqs. (13) and (14) [7, 9, 10] to conduct the fitting calculation and obtain n and k
values, thereby obtaining � drx curve data under different temperatures and strain rates:
X kdr x
rec dr x
sat ss
c
p
n
�
�
�
� � �
�
�
�
�
�
�
�
�
�
�
�
�� �
� �
� �
�
1 exp
�
�
�
�
�
�
��
�
�
�
��
, � � �c ss , (13)
ln ( ln ( )) ln ln ,� � � �
�
1 X k ndr x
c
p
� �
�
� � �c ss . (14)
3. Experimental Results and Discussion. Function relationship in Eq. (7) was used
to conduct fitting calculation of measured stress-strain data. To ensure precision of fitting
calculation of f ( )� function, g ( )� function was designed as Eq. (15), and a0 , a1, ..., a9
as the parameters to be determined. In Fig. 3, taking temperature of 1023 K as examples,
the fitting calculated stress was compared to measured stress, indicating that the stress point
of fitting calculation was identical to measured stress curve at the temperatures from 773 to
1173 K and strain rates from 0.001 to 1 s�1. It was revealed that f ( )� function could be
used to calculate � rec and � drx :
g a a a a a a( ) ln ln ln (ln )� � � � � � � � �� � � � � � �0 1 2 3 4
2
5
2
ISSN 0556-171X. Ïðîáëåìè ì³öíîñò³, 2019, ¹ 1 131
Construction and Verification of the Constitutive Model ...
� � � �a a a a6
2
7
2
8
3
9
3� � � �(ln ) (ln ) . (15)
Equation (11) was used to calculate the strain hardening rate. Figure 4 shows the
curves of strain hardening rate � and flow stress � at temperature of 873 K. From point
of intersection of � �� curve, peak stress and steady state stress can be determined in
proper order. Figure 4 shows under strain rate 1 s�1, � �� curve is always located above
the zero curve because under such deformation conditions there is no obvious dynamic
recrystallization in pure copper. Accordingly, the stresses corresponding to the minimum
curve values of the peak stress and steady state stress were taken. The same method was
used to obtain peak stress and steady state stress at different temperatures and strain rates.
Within the framework of the proposed method, the peak stress � p , steady-state
stress � ss , critical stress � c , and saturated stress � sat were calculated under different
132 ISSN 0556-171X. Ïðîáëåìè ì³öíîñò³, 2019, ¹ 1
S. H. Huang, Y. Wu, Z. D. Zhao, and X. S. Xia
Fig. 3. Comparison of predicted flow stresses and the experimental data at T �1023 K.
Fig. 4. Curves of strain hardening rate vs strain at T=873 K.
temperatures and strain rates, as shown in Fig. 5. Parameters related to Fig. 5 can be used
to determine Eqs. (1) and (2). The values of n and k can be obtained by linear regression
between ln[ ln( )]� �1 X drx and ln[( ) ],� � �� c p which is 1.49735 and 0.562980662,
respectively.
When � �ss 09163. , stress increases with the increment of strain, then there occurs
the phenomenon of second work hardening. To fit relationship of the second work
hardening stress-strain under different temperatures and strain rates, the Johnson–Cook
model [14–16], namely Eq. (16), was selected to conduct fitting analysis of stress of the
second work hardening. Research results [15] show that the Johnson–Cook model treats the
work hardening, strain rate, and thermal effects as independent factors, and does not
consider their coupled effect. Moreover, the determination of reference condition is often
inappropriate [16]. To avoid these shortcomings, the Johnson–Cook model had been
refined in this paper, namely, Eq. (17) was used to conduct fitting calculation of the second
work hardening stress–strain data under different temperatures and strain rates:
� � �
�
�
� � �
�
��
�
�� �
�
�
�
��
�
��( ) ln
�
�
0 1 1r pl
B
r
r
m
q
A C
T T
T T
�
�
�
�
�
�, (16)
ISSN 0556-171X. Ïðîáëåìè ì³öíîñò³, 2019, ¹ 1 133
Construction and Verification of the Constitutive Model ...
a b
c d
Fig. 5. Temperature and strain rates vs peak stress (a), steady state stress (b), critical stress (c), and
saturated stress (d).
ln exp[ ln ln� � � � � �wh a a a a a� � � � � �0 1 2 3 4
2
� �
�
�
�
�
�
�
�
�
�
� �
�
a c c
T
b b
5
2
0 11
0001
1
7730
1
(ln ) ] ln
�
.
�
�
100
2
3
�
�
�
�
�
�
�
�
�
� !
b b
! �
�
�
�
�
�
�
�
�
�
� �
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c c
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, � �ss 09163. . (17)
To sum up, Eqs. (1), (2), and (17) take into account the effect of dynamic recovery,
dynamic recrystallization, and secondary work hardening on the stress, which make it
possible to calculate the stresses under different temperatures and strain rates. The
comparison of the experimental data and predictions is depicted in Fig. 2. It can be seen
that there is a good agreement between the predicted values and the experimental data.
To verify the validity and effectiveness of the developed program, the finite element
method (FEM) simulations were performed to analyze upsetting process under different
experimental conditions. The billet size of FEM simulations was identical to size of thermal
simulation test cylindrical specimens, i.e., diameter of 8 mm and height of 12 mm, the time
step of FEM simulations accords with that of the thermal simulation test. Simulation proof
of upsetting process was performed. Figure 6 shows the variation of loading force with
strain under four different strain rates 0.001, 0.01, 0.1, and 1 s�1 at the deformation
temperatures of 1073 K. Generally speaking, it illustrates that the loading force simulated
by FEM fits in well with the results of compression test. In other words, the simulation
results confirm that the developed constitutive equations well describe the flow behavior of
pure copper during hot forming process.
Conclusions. The critical conditions for DRX (critical strain and critical stress) are
acquired based on the flow stress analysis, and calculation is conducted to obtain saturation
stress and parameter r, thereby establishing flow stress function of the dynamical recover.
134 ISSN 0556-171X. Ïðîáëåìè ì³öíîñò³, 2019, ¹ 1
S. H. Huang, Y. Wu, Z. D. Zhao, and X. S. Xia
Fig. 6. Variation of load force with strain for pure copper under deformation temperature of 1073 K.
The Avrami’s power n and constant k of deformation in the present working conditions
are determined as 1.49735 and 0.562980662, respectively. Furthermore, flow stress function
of dynamical recrystallization is established. The refined Johnson–Cook model is used in
fitting of secondary work hardening stress under different temperatures and strain rates
conditions.
A two-dimensional hot upsetting experiment was simulated, it is confirmed that the
proposed constitutive equations can be used in numerical simulation in upsetting process of
pure copper. It indicates that the developed constitutive equations well describe the flow
behavior of pure copper during hot forming process.
Acknowledgments. This research is funded by Chongqing Research Program of Basic
Research and Frontier Technology (No. CSTC2015JCYBX0115).
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Construction and Verification of the Constitutive Model ...
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Received 15. 03. 2018
136 ISSN 0556-171X. Ïðîáëåìè ì³öíîñò³, 2019, ¹ 1
S. H. Huang, Y. Wu, Z. D. Zhao, and X. S. Xia
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/ENU (Use these settings to create Adobe PDF documents best suited for high-quality prepress printing. Created PDF documents can be opened with Acrobat and Adobe Reader 5.0 and later.)
>>
/Namespace [
(Adobe)
(Common)
(1.0)
]
/OtherNamespaces [
<<
/AsReaderSpreads false
/CropImagesToFrames true
/ErrorControl /WarnAndContinue
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/IncludeNonPrinting false
/IncludeSlug false
/Namespace [
(Adobe)
(InDesign)
(4.0)
]
/OmitPlacedBitmaps false
/OmitPlacedEPS false
/OmitPlacedPDF false
/SimulateOverprint /Legacy
>>
<<
/AddBleedMarks false
/AddColorBars false
/AddCropMarks false
/AddPageInfo false
/AddRegMarks false
/ConvertColors /ConvertToCMYK
/DestinationProfileName ()
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/Downsample16BitImages true
/FlattenerPreset <<
/PresetSelector /MediumResolution
>>
/FormElements false
/GenerateStructure false
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/MultimediaHandling /UseObjectSettings
/Namespace [
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(CreativeSuite)
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]
/PDFXOutputIntentProfileSelector /DocumentCMYK
/PreserveEditing true
/UntaggedCMYKHandling /LeaveUntagged
/UntaggedRGBHandling /UseDocumentProfile
/UseDocumentBleed false
>>
]
>> setdistillerparams
<<
/HWResolution [2400 2400]
/PageSize [612.000 792.000]
>> setpagedevice
|